Single Crystal Graphene or Polycrystalline Graphene Matrix Composite Containing Carbon-Based Fillers

ABSTRACT

A process for producing a unitary graphene matrix composite, the process comprising: (a) preparing a graphene oxide gel having graphene oxide molecules dispersed in a fluid medium, wherein the graphene oxide gel is optically transparent or translucent; (b) mixing a carbon or graphite filler phase in said graphene oxide gel to form a slurry; (c) dispensing said slurry onto a surface of a supporting substrate or a cavity of a molding tool; (d) partially or completely removing the fluid medium from the slurry to form a composite precursor; and (e) heat-treating the composite precursor to form the unitary graphene composite at a temperature higher than 100° C. This composite exhibits a combination of exceptional thermal conductivity, electrical conductivity, mechanical strength, surface hardness, and scratch resistance.

CROSS REFERENCE TO RELATED APPLICATIONS

The present application is a continuation of pending U.S. patentapplication Ser. No. 14/756,852, filed on Oct. 22, 2015, which is adivisional of U.S. patent application Ser. No. 13/694,468 filed on Dec.5, 2012, both of which are hereby incorporated by reference.

FIELD OF THE INVENTION

The present invention relates generally to the field of graphiticmaterials for heat dissipation applications and, more particularly, to agraphene matrix composite containing a graphene oxide-derived unitarygraphene matrix material and a carbon or graphite filler orreinforcement phase dispersed in or bonded by the graphene matrixmaterial. This unitary graphene matrix composite exhibits a combinationof exceptionally high thermal conductivity, high electricalconductivity, high mechanical strength, good surface scratch resistance,and good hardness.

BACKGROUND OF THE INVENTION

Carbon is known to have five unique crystalline structures, includingdiamond, fullerene (0-D nano graphitic material), carbon nano-tube (1-Dnano graphitic material), graphene (2-D nano graphitic material), andgraphite (3-D graphitic material).

The carbon nano-tube (CNT) refers to a tubular structure grown with asingle wall or multi-wall. Carbon nano-tubes have a diameter on theorder of a few nanometers to a few hundred nanometers. Its longitudinal,hollow structure imparts unique mechanical, electrical and chemicalproperties to the material. CNT is a 1-D (one-dimensional) nano carbonor 1-D nano graphite material.

Bulk natural flake graphite is a 3-D graphitic material with eachparticle being composed of multiple grains (or graphite single crystalsor crystallites) with grain boundaries (amorphous or defect zones)demarcating neighboring graphite single crystals. Each grain is composedof multiple graphene planes oriented parallel to one another. A grapheneplane in a graphite crystallite is composed of carbon atoms occupying atwo-dimensional, hexagonal lattice. In a given grain or single crystal,the graphene planes are stacked and bonded via van der Waal forces inthe crystallographic c-direction (perpendicular to the graphene plane orbasal plane). Although all the graphene planes in one grain are parallelto one another, typically the graphene planes in one grain and thegraphene planes in an adjacent grain are different in orientation. Inother words, the orientations of the various grains in a graphiteparticle typically differ from one grain to another.

A graphite single crystal (crystallite) per se is anisotropic with aproperty measured along a direction in the basal plane (crystallographica- or b-axis direction) being dramatically different than if measuredalong the crystallographic c-axis direction (thickness direction). Forinstance, the thermal conductivity of a graphite single crystal can beup to approximately 1,920 W/mK (theoretical) or 1,800 W/mK(experimental) in the basal plane (crystallographic a- and b-axisdirections), but that along the crystallographic c-axis direction isless than 10 W/mK (typically less than 5 W/mK). Consequently, a naturalgraphite particle composed of multiple grains of different orientationsexhibits an average property between these two extremes. It would behighly desirable in many applications to produce a bulk graphiteparticle (containing single or multiple grains) having sufficientlylarge dimensions and having all graphene planes being essentiallyparallel to one another along one desired direction. For instance, it ishighly desirable to have one large-size graphite particle (e.g. aunitary layer of multiple graphene planes) having the c-axis directionsof all the graphene planes being substantially parallel to one another)and having a sufficiently large length/width for a particularapplication (e.g. >5 cm² for use as a heat-spreading sheet on a CPU of asmart phone). Thus far, it has not been possible to produce this type oflarge-size unitary graphene entity from existing natural or syntheticgraphite particles.

The constituent graphene planes of a graphite crystallite can beextracted or isolated from a graphite crystallite to obtain individualgraphene sheets of carbon atoms. An isolated, individual graphene sheetis commonly referred to as single-layer graphene. A stack of multiplegraphene planes bonded through van der Waals forces in the thicknessdirection with an inter-graphene plane spacing of 0.335 nm is commonlyreferred to as a multi-layer graphene. A multi-layer graphene platelethas up to 300 layers of graphene planes (<100 nm in thickness), but moretypically up to 30 graphene planes (<10 nm in thickness), even moretypically up to 20 graphene planes (<7 nm in thickness), and mosttypically up to 10 graphene planes (commonly referred to as few-layergraphene in scientific community). Single-layer graphene and multi-layergraphene sheets are collectively called “nano graphene platelets”(NGPs). Graphene or NGP is a new class of carbon nano material (a 2-Dnano carbon) that is distinct from the 0-D fullerene, the 1-D CNT, andthe 3-D graphite.

Our research group pioneered the development of graphene materials andrelated production processes as early as 2002: (1) B. Z. Jang and W. C.Huang, “Nano-scaled Graphene Plates,” U.S. Pat. No. 7,071,258 (Jul. 4,2006), application submitted in October 2012; (2) B. Z. Jang, et al.“Process for Producing Nano-scaled Graphene Plates,” U.S. patentapplication Ser. No. 10/858,814 (Jun. 3, 2004); and (3) B. Z. Jang, A.Zhamu, and J. Guo, “Process for Producing Nano-scaled Platelets andNanocomposites,” U.S. patent application Ser. No. 11/509,424 (Aug. 25,2006).

NGPs are typically obtained by intercalating natural graphite particleswith a strong acid and/or oxidizing agent to obtain a graphiteintercalation compound (GIC) or graphite oxide (GO), as illustrated inFIG. 1(a) (process flow chart) and FIG. 1(b) (schematic drawing). Thisis most often accomplished by immersing natural graphite powder (20 inFIG. 1(a) and 100 in FIG. 1(b)) in a mixture of sulfuric acid, nitricacid (an oxidizing agent), and another oxidizing agent (e.g. potassiumpermanganate or sodium chlorate). The resulting GIC (22 or 102) isactually some type of graphite oxide (GO) particles. This GIC is thenrepeatedly washed and rinsed in water to remove excess acids, resultingin a graphite oxide suspension or dispersion, which contains discreteand visually discernible graphite oxide particles dispersed in water.There are two processing routes to follow after this rinsing step:

Route 1 involves removing water from the suspension to obtain“expandable graphite,” which is essentially a mass of dried GIC or driedgraphite oxide particles. Upon exposure of expandable graphite to atemperature in the range of typically 800-1,050° C. for approximately 30seconds to 2 minutes, the GIC undergoes a rapid expansion by a factor of30-300 to form “graphite worms” (24 or 104), which are each a collectionof exfoliated, but largely un-separated or still interconnected graphiteflakes. A SEM image of graphite worms is presented in FIG. 2(a).

In Route 1A, these graphite worms (exfoliated graphite or “networks ofinterconnected/non-separated graphite flakes”) can be re-compressed toobtain flexible graphite sheets or foils (26 or 106) that typically havea thickness in the range of 0.125 mm (125 μm)-0.5 mm (500 μm). One maychoose to use a low-intensity air mill or shearing machine to simplybreak up the graphite worms for the purpose of producing the so-called“expanded graphite flakes” (108) which contain mostly graphite flakes orplatelets thicker than 100 nm (hence, not a nano material bydefinition).

Exfoliated graphite worms, expanded graphite flakes, and therecompressed mass of graphite worms (commonly referred to as flexiblegraphite sheet or flexible graphite foil) are all 3-D graphiticmaterials that are fundamentally different and patently distinct fromeither the 1-D nano carbon material (CNT) or the 2-D nano carbonmaterial (graphene).

As disclosed by M. Smalc, et al, U.S. Pat. No. 7,292,441 (Nov. 6, 2007)and No. 6,982,874 (Jun. 3, 2006), and J. W. Tzeng, U.S. Pat. No.6,482,520 (Nov. 19, 2002), these flexible graphite (FG) foils can beused as a heat spreader material, but exhibiting a maximum in-planethermal conductivity of typically less than 500 W/mK (more typically<300 W/mK) and in-plane electrical conductivity no greater than 1,500S/cm. These low conductivity values are a direct result of the manydefects, wrinkled or folded graphite flakes, interruptions or gapsbetween graphite flakes, and non-parallel flakes (e.g. SEM image in FIG.2(b)). Many flakes are inclined with respect to one another at a verylarge angle (e.g. mis-orientation of 20-40 degrees).

In Route 1B, the exfoliated graphite is subjected to high-intensitymechanical shearing (e.g. using an ultrasonicator, high-shear mixer,high-intensity air jet mill, or high-energy ball mill) to form separatedsingle-layer and multi-layer graphene sheets (collectively called NGPs,33 or 112), as disclosed in our U.S. application Ser. No. 10/858,814.Single-layer graphene can be as thin as 0.34 nm, while multi-layergraphene can have a thickness up to 100 nm. In the present application,the thickness of multi-layer NGPs is typically less than 20 nm.

Route 2 entails ultrasonicating the graphite oxide suspension for thepurpose of separating/isolating individual graphene oxide sheets fromgraphite oxide particles. This is based on the notion that theinter-graphene plane separation bas been increased from 0.335 nm innatural graphite to 0.6-1.1 nm in highly oxidized graphite oxide,significantly weakening the van der Waals forces that hold neighboringplanes together. Ultrasonic power can be sufficient to further separategraphene plane sheets to form separated, isolated, or discrete grapheneoxide (GO) sheets. These graphene oxide sheets can then be chemically orthermally reduced to obtain “reduced graphene oxides” (RGO) typicallyhaving an oxygen content of 0.001%-10% by weight, more typically0.01%-5% by weight.

For the purpose of defining the claims of the instant application, NGPsinclude single-layer and multi-layer graphene or reduced graphene oxidewith an oxygen content of 0-10% by weight, more typically 0-5% byweight, and preferably 0-2% weight. Pristine graphene has essentially 0%oxygen. Graphene oxide (including RGO) can have 0.001%-46% by weight ofoxygen. The graphene oxide gel, to be described in detail later,typically contains 20-46% by weight oxygen immediately after removal ofthe liquid from the GO gel, but prior to a subsequent heat treatment.The graphene oxide gel-derived unitary graphene layer or graphene singlecrystal of the present invention typically has an oxygen content of0.01% to 5% by weight, more typically <<2% by weight. This grapheneoxide gel-derived graphene material, reinforced with a filler phase(e.g. CNTs and carbon fibers), constitutes the presently inventedunitary graphene matrix composite. This composite is made by forming amixture of the filler particles with the GO gel (e.g. by impregnating aCNT mat with the GO gel or by dispersing the CNTs in a GO gel to form aslurry), followed by removal of liquid from the gel and heat-treatmentof the resulting GO-filler solid mixture (for the purpose of reducingand re-graphitizing GO molecules). The heat treatment serves tochemically link GO molecules to form a 2-D or 3-D network of chemicallybonded graphene molecules of essentially infinite molecular weights, andto drastically reduce the oxygen content of GO down to below 10% byweight, more typically <5%, further more typically <2%, and mosttypically <<1% (only trace amount if the heat treatment temperature issufficiently high and heat treatment time sufficiently long).

It may be noted that flexible graphite foils (obtained by re-compressingor roll-pressing exfoliated graphite worms) for electronic devicethermal management applications (e.g. as a heat spreader) have thefollowing major deficiencies:

-   -   (1) As indicated earlier, flexible graphite (FG) foils exhibit a        relatively low thermal conductivity, typically <500 W/mK and        more typically <300 W/mK.    -   (2) Flexible graphite foils are also of low strength and poor        structural integrity. The high tendency for flexible graphite        foils to get torn apart makes them difficult to handle in the        process of integrating them in a microelectronic device.    -   (3) Another very subtle, largely ignored or overlooked, but        critically important feature of FG foils is their high tendency        to get flaky with graphite flakes easily coming off from FG        sheet surfaces and emitting out to other parts of a        microelectronic device. These highly electrically conducting        flakes (typically 1-200 μm in lateral dimensions and >100 nm in        thickness) can cause internal shorting and failure of electronic        devices.    -   (4) For this reason, it is necessary to apply a protective resin        coating onto a surface or on both surfaces of a flexible        graphite foil in order to prevent graphite flakes from being        released. This resin coating is typically not a thermally or        electrically conductive material that is often an undesirable        feature in a situation where high conductivity is required. In        other situations where electrical insulation or isolation is        required, this resin layer can present some issues (e.g.        mis-match in coefficients of thermal expansion and elastic        constants between the FG layer and the resin coating, resulting        in delamination or peeling-off after some number of thermal        cycles).

The presently invented unitary graphene layer itself and itscarbon/graphite filler-reinforced version (the unitary graphene matrixcomposite) were invented to address the aforementioned issues and weresurprisingly found to overcome essentially all of these problemsassociated with FG foils.

Other sheet-like graphitic materials that can be used as a heat spreaderor thermal interface material include resin-free or resin-impregnatedversions of carbon nano-tube (CNT) paper (e.g. Bucky paper), carbonfiber mat (e.g. carbon nano-fiber or CNF mat), and carbon paper (e.g.made of short carbon fibers). These graphitic sheets also suffer fromsimilar shortcomings as FG foils. For instance, although individual CNTor CNF filaments alone can exhibit a high thermal conductivity(1,500-3000 W/mK), the resulting CNT or CNF paper or mat typicallyexhibit an in-plane thermal conductivity less than 100 W/mK and oftenless than 10 W/mK, likely due to the few and poor contacts betweenindividual CNT or CNF filaments, providing insufficient cross-sectionsfor electron flow or even impeding electron flow. Further, the contactbetween a sheet-like graphitic layer and a heat source is usually poordue to limited contact surfaces between such a graphitic layer (e.g. CNTpaper) and a rigid device component (e.g. a CPU in a mobile phone). Thisresults in an ineffective heat transfer between the heat source and thegraphitic layer. Additionally, these mats or paper structures, ifimpregnated with a resin (e.g. epoxy) for improved strength andrigidity, actually exhibit even lower thermal conductivity andelectrical conductivity.

Similarly, the NGPs (including discrete platelets of pristine graphene,GO, and GRO), when packed into a film or paper sheet (34 or 114) ofnon-woven aggregates, typically do not exhibit a high thermalconductivity. The thermal conductivity is found to be higher than 1,000W/mK only when the film or paper is cast and pressed into a sheet havinga thickness lower than 10 μm, and higher than 1,500 W/mK only when thefilm or paper is cast and greatly pressed into a sheet having athickness lower than 1 μm (which is mechanically weak). This is reportedin our earlier U.S. patent application Ser. No. 11/784,606 (Apr. 9,2007). However, ultra-thin film or paper sheets (<10 μm) are difficultto produce in mass quantities, and difficult to handle when one tries toincorporate these thin films as a heat spreader material during themanufacturing of microelectronic devices.

In general, a paper-like structure or mat made from platelets ofgraphene, GO, or RGO (e.g. those paper sheets prepared byvacuum-assisted filtration process) exhibit many defects, wrinkled orfolded graphene sheets, interruptions or gaps between platelets, andnon-parallel platelets (e.g. SEM image in FIG. 3(b)), leading torelatively poor thermal conductivity, low electric conductivity, and lowstructural strength. These papers or aggregates of discrete NGP, GO orRGO platelets also have a tendency to get flaky, emitting conductiveparticles into air.

Our earlier application (U.S. application Ser. No. 11/784,606) furtherdisclosed a mat, film, or paper of NGPs infiltrated with a metal, glass,ceramic, resin, and CVD carbon matrix material (graphene being thefiller or reinforcement phase, not the matrix phase). Subsequently,Haddon, et al (US Pub. No. 2010/0140792, Jun. 10, 2010) also reportedNGP thin film and NGP-reinforced polymer matrix composites for thermalmanagement applications. The processes used by Haddon et al to produceNGPs are identical to those disclosed much earlier by us (Jang, et al.U.S. patent application Ser. No.10/858,814 (Jun. 3, 2004)). TheNGP-reinforced polymer matrix composites, as an intended thermalinterface material, have very low thermal conductivity, typically <<2W/mK. The NGP films of Haddon, et al are essentially non-wovenaggregates of discrete graphene platelets, identical to those of ourearlier invention (U.S. application Ser. No. 11/784,606). Again, theseaggregates have a great tendency to have graphite particles flaking andseparated from the film surface, creating internal shorting problem forthe electronic device containing these aggregates. They also exhibit lowthermal conductivity unless made into thin films (10 nm-300 nm, asreported by Haddon, et al) which are very difficult to handle in a realdevice manufacturing environment. Balandin, et al (US Pub. No.2010/0085713, Apr. 8, 2010) also disclosed a graphene layer produced byCVD deposition or diamond conversion for heat spreader application. Morerecently, Kim, et al (N. P. Kim and J. P. Huang, “Graphene NanoplateletMetal Matrix,” US Pub. No. 2011/0108978, May 10, 2011) reported metalmatrix infiltrated NGPs. However, metal matrix material is too heavy andthe resulting metal matrix composite does not exhibit a high thermalconductivity.

Another prior art material for thermal management application is thepyrolitic graphite film. The lower portion of FIG. 1(a) illustrates atypical process for producing prior art pyrolitic graphitic films orsheets from a polymer. The process begins with carbonizing a polymerfilm 46 at a carbonization temperature of 500-1,000° C. for 2-10 hoursto obtain a carbonized material 48, which is followed by agraphitization treatment at 2,500-3,200° C. for 5-24 hours to form agraphitic film 50. This is a slow, tedious, and energy-intensiveprocess. Furthermore, carbonization of certain polymers (e.g.polyacrylonitrile) involves the emission of toxic species.

A second type of pyrolytic graphite is produced by high temperaturedecomposition of hydrocarbon gases in vacuum followed by deposition ofthe carbon atoms to a substrate surface. This is essentially a chemicalvapor deposition (CVD) process. In particular, highly oriented pyroliticgraphite (HOPG) is the material produced by the application of uniaxialpressure on deposited pyrocarbon or pyrolytic graphite at very hightemperatures (typically 3,000-3,300° C.). This entails athermo-mechanical treatment of combined mechanical compression andultra-high temperature for an extended period of time in a protectiveatmosphere; a very expensive, energy-intensive, and technicallychallenging process. The process requires high vacuum and ultra-hightemperature equipment that is not only very expensive to make but alsovery expensive and difficult to maintain. Even with such extremeprocessing conditions, the resulting PG (including HOPG) still possessesmany defects, grain boundaries, and mis-orientations (neighboringgraphene planes not parallel to each other), resulting inless-than-satisfactory in-plane properties. Typically, the best preparedHOPG sheet or block remains far from being a graphite single crystal;instead, it typically still contains many grains or single crystals anda vast amount of grain boundaries and defects. In general, the PG orHOPG is free from any element than carbon.

Similarly, the most recently reported graphene thin film (<2 nm)prepared by catalytic CVD of hydrocarbon gas (e.g. C₂H₄) on Ni or Cusurface is not a single-grain crystal, but a poly-crystalline structurewith many grain boundaries and defects [e.g., Edwards R S, Coleman K S.,“Graphene Film Growth on Polycrystalline Metals,” Accounts of Chem. Res.2012 Aug 15]. With Ni or Cu being the catalyst, carbon atoms obtainedvia decomposition of hydrocarbon gas molecules at 800-1,000° C. aredeposited onto Ni or Cu foil surface to form a sheet of single-layer orfew-layer graphene that is poly-crystalline. The grains are typicallymuch smaller than 100 μm in size and, more typically, smaller than 10 μmin size. These graphene thin films, being optically transparent andelectrically conducting, are intended for applications such as the touchscreen (to replace indium-tin oxide or ITO glass) or semiconductor (toreplace silicon, Si). However, these polycrystalline graphene films arenot sufficiently thermally conducting (too many grains or too much grainboundaries, and all grains being oriented in different directions) andnot sufficiently thick for use as a heat spreader in an electronicdevice.

Thus, it is an object of the present invention to provide a grapheneoxide (GO) gel-derived unitary graphene layer (monolithic graphene film)and its composite version (containing a carbon/graphite filler phasedispersed in or bonded by a unitary graphene matrix derived from a GOgel), which exhibit a thermal conductivity comparable to or greater thanthat of the PG, HOPG, or CVD graphene film.

It is a specific object of the present invention to provide a new classor classes of materials (i.e., a GO gel-derived unitary graphenemonolithic and its composite materials) that have the followingcharacteristics (separately or in combination) that distinguishthemselves from PG, HOPG, CVD graphene film, flexible graphite sheets,flexible graphite composites, conventional resin matrix composites andcarbon matrix composites:

-   (1) This unitary graphene material, standing alone or as the matrix    material in a composite, is an integrated graphene entity that is    either a graphene single crystal (single grain only) or a    poly-crystal (multiple grains but typically having incomplete grain    boundaries). Typically and preferably, with some compression or    shearing stresses exerted on the GO and a subsequent heat treatment,    the unitary graphene composite has all the graphene planes in all    the grains being essentially oriented parallel to one another (i.e.,    the crystallographic c-axis of all grains pointing in an identical    direction).-   (2) The unitary graphene matrix is an integrated graphene entity    that is not an aggregate or stack of multiple discrete graphite    flakes or discrete platelets of graphene or GO, and does not contain    any discernible or discrete flake/platelet derived from the original    GO gel.-   (3) This integrated graphene matrix is not made by gluing or bonding    discrete flakes/platelets together with a binder, linker, or    adhesive. Instead, GO molecules in the GO gel are chemically merged,    mainly in an edge-to-edge manner (forming 2-D giant graphene    molecules) but possibly also with adjacent GO molecules below or    above (forming 3-D network of graphene chains). Through joining or    forming of covalent bonds with one another, the GO molecules are    adhered into an integrated graphene entity (the unitary graphene    matrix), without using any externally added linker or binder    molecules or polymers. In the presence of carbon or graphite filler    particles (e.g. carbon black particles or CNTs), the GO molecules    are also capable of acting as a binder or adhesive that chemically    bonds these carbon/graphite filler particles together to form a    strong composite.-   (4) This unitary or monolithic graphene matrix (a single crystal or    poly-crystal with essentially all graphene planes having an    identical crystallographic c-axis) is derived from a GO gel, which    is in turn obtained from heavy oxidation of natural graphite or    artificial graphite particles originally having multiple graphite    crystallites. Prior to being chemically oxidized to become GO gel,    these starting or original graphite crystallites have an initial    length (L_(a) in the crystallographic α-axis direction), initial    width (L_(b) in the b-axis direction), and thickness (L_(c) in the    c-axis direction). The resulting unitary graphene entity typically    has a length or width significantly greater than the L_(a) and L_(b)    of the original graphite crystallites.-   (5) It may be noted that there has been numerous reports on    “graphene composites.” However, these “graphene composites” make use    of discrete pristine graphene sheets, graphene oxide platelets, or    reduced graphene oxide platelets as the reinforcement phase which is    dispersed in a matrix material selected from a resin (to form a    resin matrix composite), a metal (metal matrix composite), a carbon    (carbon matrix composite), a glass (glass matrix composite), or a    ceramic (ceramic matrix composite). In these prior art “graphene    composites,” graphene sheets/platelets are the discrete and    dispersed phase, not the matrix phase (or continuous phase); these    discrete graphene sheets/platelets are bonded and protected by a    matrix material, such as a resin, metal, carbon (CVD carbon,    amorphous carbon, or polymeric carbon), glass, or ceramic. In stark    contrast or completely oppositely, in the presently invented unitary    graphene matrix composite, graphene is the matrix material that    serves to bond, adhere, and protect the dispersed filler phase, such    as CNT and carbon black (CB) particles. CNT or CB particles are    dispersed in and protected by the unitary graphene matrix.    Typically, the graphene matrix is a continuous, unified, or    integrated material phase.

The present invention also provides a method or process for producingsuch a GO gel-derived unitary graphene entity (or a graphene singlecrystal, including a graphene poly-crystal with an incomplete grainboundary) and the graphene matrix composite. This unitary grapheneentity can be used as a standalone layer (e.g., as a heat spreader) oras a matrix material for a composite containing a carbon or graphitefiller phase.

Another object of the present invention is to provide a cost-effectiveprocess of producing a GO-derived graphene monolith and a graphenematrix composite that exhibit a combination of exceptional thermalconductivity, electrical conductivity, mechanical strength, surfacehardness, and scratch resistance unmatched by any thin-film graphiticmaterial of comparable thickness range.

In particular, the present invention provides a process for producing aunitary or monolithic graphene layer or graphene single crystal (as astandalone material or as a matrix material) from a GO gel. This processdoes not involve or require an ultrahigh temperature as is absolutelyrequired of the processes for producing pyrolytic graphite (includingHOPG) from either carbonized polymers (e.g. polyimide) or using the CVDdeposition. The presently invented process is simpler (hence, morereliable), less energy-intensive, and highly scalable.

This thermally and electrically conductive graphene monolith or graphenematrix composite can be used for thermal management applications (e.g.for use as a heat spreader) in a microelectronic device, such as amobile phone (including a smart phone), a notebook computer, a tablet,an e-book, a telecommunication device, and any hand-held computingdevice or portable microelectronic device.

It is another object of the present invention to provide a GO-derivedunitary graphene entity and graphene matrix composite that exhibit acombination of exceptional thermal conductivity, electricalconductivity, mechanical strength, surface smoothness, surface hardness,and scratch resistance unmatched by any thin-film material of comparablethickness range.

It is a specific object of the present invention to provide a highlyconductive graphene matrix composite that meets the following technicalrequirements (a) in-plane thermal conductivity greater than 600 W/mK(preferably greater than 1,000 W/mK, and further preferably greater than1,700 W/mK); (b) in-plane electrical conductivity greater than 2,000S/cm (preferably >3,000 S/cm, more preferably >5,000 S/cm, and mostdesirably >10,000 S/cm); (c) Rockwell surface hardness value >60(preferably >80); and/or (d) a tensile strength greater than 80 MPa(preferably >100 MPa, more preferably >150 MPa, and most preferably >200MPa).

SUMMARY OF THE INVENTION

The present invention provides a unitary graphene matrix compositecomprising: (a) A unitary graphene matrix containing closely packed andchemically bonded graphene planes having an inter-graphene plane spacingof 0.335 to 0.40 nm and an oxygen content of 0.001% to 10% by weight,which unitary graphene matrix is obtained from heat-treating a grapheneoxide gel at a temperature higher than 100° C. and contains no discretegraphene platelets derived from the graphene oxide gel; and (b) A carbonor graphite filler phase selected from a carbon or graphite fiber,carbon or graphite nano-fiber, carbon nano-tube, carbon nano-rod,meso-phase carbon particle, meso-carbon micro-bead, exfoliated graphiteflake with a thickness greater than 100 nm, exfoliated graphite orgraphite worm, coke particle, needle coke, carbon black or acetyleneblack particle, activated carbon particle, or a combination thereof. Thecarbon or graphite filler phase occupies a weight fraction of 0.01% to99% based on the total composite weight and the carbon or graphitefiller phase is in a particulate, filamentary, or rod-like formdispersed in the unitary graphene matrix.

Preferably, the carbon or graphite filler phase occupies a weightfraction from 0.1% to 70% based on the total composite weight. Thegraphene matrix composite preferably has a physical density of at least1.5 g/cm³ or a porosity level lower than 20%, and more preferably has aphysical density of at least 1.7 g/cm³ or a porosity level lower than10%. Preferably and typically, the carbon or graphite filler ischemically bonded by the unitary graphene matrix. It is most surprisingthat this unitary graphene matrix, prepared through the route of a GOgel, is capable of chemically bonding to a filler phase and that theconstituent GO molecules in a GO gel mass are capable of chemicallybonding and merging with one another to form an integrated 2-D or 3-Dnetwork of aromatic chains or giant graphene molecules of essentiallyinfinite molecular weight, much like a 3-D network of cross-linkedpolymer chains. Chemical analyses, including various spectroscopystudies, have demonstrated that these chemically bonded graphenemolecules contain a combination of sp² and sp³ electronicconfigurations.

It may be noted that the unitary graphene matrix material, when preparedalone without the presence of the carbon or graphite filler phase, canbe made into a unitary graphene layer or graphene single crystal. Thisunitary graphene layer or graphene single crystal would contain closelypacked and bonded parallel graphene planes having an inter-grapheneplane spacing of 0.335 to 0.40 nm and an oxygen content of 0.01% to 10%by weight. This unitary graphene layer or graphene single crystal can beobtained from heat-treating a graphene oxide gel at a temperature higherthan 100° C., wherein an average mis-orientation angle between twographene planes is less than 10 degrees, preferably and typically lessthan 5 degrees. The graphene single crystal, prepared alone without thepresence of a filler, refers to the single-grain or single-domaingraphene or poly-crystalline structure (but having an incomplete grainboundary) in which most of the graphene planes in all grain(s) areessentially parallel to one another. In this unitary graphene orgraphene monolith, there contains no discrete graphite flake or grapheneplatelet derived from the graphene oxide gel.

In the unitary graphene matrix composite prepared in the presence of afiller phase, the chemically bonded graphene planes also can be parallelto one another. In the unitary graphene matrix composite, the unitarygraphene matrix typically contains no complete grain boundary thereinand contains no discrete or discernible graphene platelet derived fromthe original graphene oxide gel. Preferably and typically, the carbon orgraphite filler is chemically bonded by the unitary matrix material inthe composite (e.g. via covalent bonds).

The process typically begins with preparation of a mass of GO gel, whichis then mixed with particles of the carbon/graphite filler phase to forma slurry mass. The slurry is formed into a desired shape, preferably ina layer form preferably with a shear stress to facilitate orientation oralignment of aromatic GO molecules. The layer is preferably less than 10mm in thickness, more preferably less than 1 mm, and most preferablyless than 500 μm in thickness prior to drying. Alternatively, thecarbon/graphite filler phase is first formed into a porous shape (e.g.mat, paper, or fabric), which is then impregnated with the GO gel. Ineither route, the liquid component of this GO gel is then partially ortotally removed and, concurrently or sequentially, this GO material issubjected to a heat treatment. This heat treatment, also herein referredto as a re-graphitization treatment, thermally converts the GO moleculesto an integrated graphene film by chemically merging individual grapheneoxide molecules primarily sideway in an edge-to-edge manner to formsignificantly larger graphene planes, but sometimes also chemicallylinking with the GO molecules below or above this graphene plane to forma 3-D molecular network.

In the unitary graphene matrix composite, the carbon or graphite filleris preferably in a form of porous woven fabric, porous non-woven fabric,porous mat, or porous paper, and the composite is made by impregnatingthe porous woven fabric, porous non-woven fabric, porous mat, or porouspaper with the graphene oxide gel prior to heat treating the grapheneoxide.

Alternatively, the carbon or graphite filler may be made into a form offiber yarns or fiber bundles impregnated with the graphene oxide gel andthe composite is made by forming the fiber yarns or bundles into adesired shape prior to heat treating. The desired shape can mean aunidirectional, bi-directional, multi-directional, angle-plied, woven,or filament-wound shape. In other words, the fiber yarns or bundles(prior, during, or after graphene oxide gel impregnation) may be formedinto a unidirectional fiber composite shape, like the shape of aconventional unidirectional continuous carbon fiber-reinforced epoxycomposite with the epoxy resin being replaced by the graphene oxide gel.It is highly surprising for us to observe that graphene oxide gel has anoutstanding adhesive power that can bond the filler phase (e.g. carbonfibers or nano-tubes) together to form a composite of exceptionalstructural integrity.

The graphene oxide gel-derived unitary or monolithic graphene layer orthe corresponding graphene matrix composite has a unique combination ofoutstanding thermal conductivity, electrical conductivity, mechanicalstrength, scratch resistance, and elimination of the possibility ofhaving surface graphite flakes or particles to “flake off” (actually,there is no discrete flake/platelet to be peeled therefrom).

The graphene oxide (GO) gel-derived unitary graphene matrix material orgraphene matrix composite has the following characteristics (separatelyor in combination):

-   -   (1) The unitary graphene matrix material itself (with or without        the presence of a filler phase) is an integrated graphene object        that is either a graphene single crystal or a poly-crystal        having multiple grains (but with incomplete or poorly delineated        grain boundaries). When made into a thin-film form (e.g. <200 μm        thick), the unitary graphene matrix is composed of multiple        graphene planes most of which are essentially oriented parallel        to one another. Specifically, the crystallographic c-axis        directions of most of the graphene planes in all the grains are        essentially pointing to an identical direction. This observation        appears to hold true when the carbon/graphite filler phase is        from 0% to 50% by weight, relatively independent of the type of        carbon/graphite filler used.    -   (2) In contrast to the paper-like sheets of expanded graphite        flakes or graphene platelets (e.g. those prepared by a        paper-making process), this integrated graphene entity (the        unitary graphene matrix material) is not an aggregate or stack        of multiple discrete graphite flakes or discrete platelets of        graphene, GO, or RGO. This is a single graphene entity or        monolith, not a simple aggregate of multiple graphite flakes        (such as FG foil) or graphene sheets (such as graphene paper or        graphene membrane). This unitary graphene entity does not        contain discrete graphite flakes or discrete graphene platelets        dispersed therein. The GO molecules do not revert back to        individual or discrete graphene platelets or graphite flakes.    -   (3) In other words, this unitary graphene matrix material is not        the result of simply exfoliating the graphene sheets or graphite        flakes (that constitute the original structure of graphite        particles) and then re-orienting these discrete sheets/flakes        along one direction. Such a simple aggregating procedure would        lead to a simple collection or stack of discrete        flakes/sheets/platelets that can be detected or discerned with        an un-assisted eye or under a low-magnification optical        microscope (×100-×1000).        -   Contrarily, the original graphite particles are heavily            oxidized, to the extent that practically every one of the            original graphene planes has been oxidized and isolated from            one another to become individual molecules that possess            highly reactive functional groups at the edge and, mostly,            on graphene planes as well. These individual hydrocarbon            molecules (containing elements such as O and H, not just            carbon atoms) are dissolved in the reaction medium (e.g.            mixture of water and acids) to form a gel-like mass, herein            referred to as GO gel. This gel is then cast onto a smooth            substrate surface, with the liquid components removed to            form a dried GO layer. When properly dispersed and heated on            a solid substrate surface, these highly reactive molecules            react and join with one another mostly in lateral directions            along graphene planes (in an edge-to-edge manner) and, in            some cases, between graphene planes as well. These linking            and merging reactions proceed in such a manner that the            molecules are chemically merged, linked, and integrated into            one single entity or monolith (not just physically stacked            or packed together). The molecules completely lose their own            original identity and they no longer are discrete            sheets/platelets/flakes. There is only one grain (or few            grains with incomplete grain boundaries) that is essentially            one huge molecule or just a few giant molecules with an            essentially infinite molecular weight. This may also be            described as a graphene single crystal (with only one grain            in the entire structure or entity, or a poly-crystal having            several grains, but typically no discernible, well-defined            grain boundaries, e.g. FIG. 3(f)). All the constituent            graphene planes are very large in lateral dimensions (length            and width) and are essentially parallel to one another.        -   In-depth X-ray diffraction, atomic force microscopy, and            electron microscopy (including selected area diffraction)            studies indicate that the graphene monolith is composed of            several huge graphene planes (with length/width            typically >>100 μm, more typically >>1 mm, and most            typically >>1 cm). These giant graphene planes are stacked            and bonded along the thickness direction (crystallographic            c-axis direction) through not just the van der Waals forces            in conventional graphite crystallites, but also covalent            bonds, Not to be limited by theory, but the studies based on            combined Raman, FTIR, and electron spectroscopy for chemical            analysis (ESCA) appear to indicate the co-existence of sp²            (dominating) and sp³ (weak but existing) electronic            configurations, not just the conventional sp² alone in            graphite.    -   (4) This integrated graphene entity is not made by gluing or        bonding discrete flakes/platelets together with a binder,        linker, or adhesive. Instead, GO molecules in the GO gel are        merged, mainly edge-to-edge through joining or forming of        covalent bonds with one another, into an integrated graphene        entity, without using any externally added linker or binder        molecules or polymers.    -   (5) This unitary or monolithic graphene entity is a single        crystal or poly-crystal (having poorly defined or incomplete        grain boundaries) with the crystallographic c-axis in all grains        being essentially parallel to each other. This entity is derived        from a GO gel, which is in turn obtained from natural graphite        or artificial graphite particles originally having multiple        graphite crystallites. Prior to being chemically oxidized, these        starting graphite crystallites have an initial length (L_(a) in        the crystallographic α-axis direction), initial width (L_(b) in        the b-axis direction), and thickness (L_(c) in the c-axis        direction). The resulting unitary graphene entity typically has        a length or width significantly greater than the L_(a) and L_(b)        of the original crystallites. The length/width of this unitary        graphene entity or that of a graphene single crystal is        typically greater than the L_(a) and L_(b) of the original        crystallites. Even the individual grains in a poly-crystalline        unitary graphene entity have a length or width significantly        greater than the L_(a) and L_(b) of the original crystallites.        They can be as large as the length or width of the unitary        graphene entity itself, not just 2 or 3 times higher than the        initial L_(a) and L_(b) of the original crystallites.    -   (6) The unitary graphene matrix composite may advantageously        contain elongated-shape or filamentary filler particles (e.g.        carbon or graphite fibers, carbon or graphite nano-fibers,        carbon nano-tubes, carbon nano-rods, and/or needle coke        particles) that have a length and a diameter or thickness. The        composite may be produced in such a manner that the        elongated-shape or filamentary particles are aligned along a        length direction so that the composite is anisotropic having an        anisotropy ratio greater than 10, wherein the anisotropy ratio        is defined as a length-direction property-to-thickness-direction        property ratio and the property is electrical conductivity,        thermal conductivity, strength, or modulus. The unitary graphene        matrix composite can have an anisotropy ratio greater than 100        for some engineering applications (e.g. heat spreader        application). For other applications, the anisotropy ratio may        be less than 10 or less than 2. An anisotropy ratio of 1 means        totally isotropic.

The unitary graphene matrix composite can have a thickness as low as 10nm, but preferably >100 nm, more preferably >1 μm, even morepreferably >10 μm. The unitary graphene matrix material alone orgraphene matrix composite preferably has a thickness less than 200 μmfor a heat spreader application, but it can be thicker. Furtherpreferably, the material has a thickness greater than 10 μm, but lessthan 200 μm. The thickness range of 20-100 μm is particularly useful formobile device thermal management applications.

The unitary graphene matrix composite of the present invention hasovercome all the major problems associated with the flexible graphitefoil produced by re-compression of exfoliated graphite worms orexfoliated graphite flakes of natural graphite and/or artificialgraphite. The flexible graphite sheet or foil prepared by re-compressing(e.g. roll-pressing) exfoliated graphite worms or flakes has a greattendency to flake off, emitting graphite flakes into air and eventuallyrelocating to a dangerous spot (e.g. where the presence of graphiteflakes could cause internal short-circuiting). Further, flexiblegraphite sheets or foils are relatively brittle and weak, and hence aredifficult to handle in an actual microelectronic device manufacturingenvironment. They also do not possess high thermal conductivity (mosttypically <300 W/mK). These and other major issues associated with theuse of flexible graphite sheets in a microelectronic device for athermal management purpose have been effectively overcome surprisinglyby the presently invented unitary graphene body.

The unitary graphene material is derived from a graphene oxide gel,which is produced from particles of natural graphite or artificialgraphite composed of multiple graphite crystallites. These crystallitestypically have an initial length L_(a) (in the crystallographic α-axisdirection) of less than 100 μm (more typically less than 10 μm), aninitial width L_(b) in the b-axis direction also of more typically lessthan 10 μm, and a thickness L_(c) in the c-axis direction (typically 0.2to 10 μm). However, the presently invented GO-derived unitary graphenelayer or graphene single crystal typically has a length or width atleast greater than twice (more typically significantly greater than 3times) the initial L_(a) or twice (more typically >3 times) the L_(b) ofthe graphite crystallites of the starting materials. The unitarygraphene layer or graphene single crystal typically has a length orwidth no less than 10 μm, more typically no less than 100 μm, and evenmore typically no less than 1 cm. They often are extended to cover theentire width of the original GO gel layer deposited on a substratesurface, which can be >100 cm as desired.

As a preferred processing condition for the unitary graphene material,if the heat-treating temperature for GO is from 100° C. to 1,000° C.,the unitary graphene matrix composite has a thermal conductivity greaterthan 400 W/mK or electrical conductivity greater than 1,000 S/cm.Alternatively, if the heat-treating temperature is from 1,000° C. to1,500° C., the resulting unitary graphene composite typically has athermal conductivity greater than 600 W/mK or electrical conductivitygreater than 2,000 S/cm. With a heat-treating temperature of from 1500°C. to 2,500° C., the unitary graphene composite typically has a thermalconductivity greater than 1,000 W/mK or electrical conductivity greaterthan 3,000 S/cm (or even >8,000 S/cm). With a heat-treating temperatureof from 2,500° C. to 3,250° C., the unitary graphene layer or graphenesingle crystal has a thermal conductivity greater than 1,500 W/mK orelectrical conductivity greater than 5,000 S/cm (typically greater than8,000 S/cm and, in many cases, greater than 10,000 S/cm). The aboverecited thermal conductivity and electrical conductivity values can besignificantly higher if the carbon/graphite filler chosen is highlyconducting (e.g. >1,750 W/mK and/or >15,000 S/cm).

The unitary graphene layer or graphene single crystal typically has anoxygen content from 0.01% to 5% by weight, more typically from 0.01% to2% by weight. If the re-graphitization temperature exceeds 2,000° C. andis conducted under very strict protective atmosphere or extremely highvacuum conditions, one can essentially eliminate oxygen.

For the preparation of the unitary graphene layer or graphene singlecrystal, the graphene oxide gel is composed of graphene oxide moleculesdispersed in an acidic medium having a pH value of no higher than 5 andthe graphene oxide molecules have an oxygen content no less than 20% byweight while in a gel state.

The GO gel is obtained by immersing a graphitic material in a powder orfibrous form (e.g. natural or artificial graphite powder or graphitefibers) in an oxidizing liquid medium in a reaction vessel at a reactiontemperature for a length of time sufficient to obtain a graphene oxidegel composed of graphene oxide molecules dispersed in the liquid medium.The graphene oxide molecules preferably and typically have an oxygencontent no less than 20% by weight (typically 20%-46% by weight ofoxygen) and a molecular weight less than 43,000 g/mole while in a gelstate. Preferably, graphene oxide molecules have a molecular weight lessthan 4,000 g/mole while in a gel state, more preferably between 200g/mole and 4,000 g/mole while in a gel state.

The unitary graphene matrix composite is produced by depositing ordispensing a layer of graphene oxide gel-filler mixture onto a surfaceof a substrate or into a mold cavity. The liquid component is thenremoved from this mixture layer of graphene oxide gel and the fillerphase. This is followed by subjecting this mixture to a heat treatmenttemperature of at least 100-150° C. for thermal reduction and/orre-graphitization. A good heat treatment temperature is from 500° C. to1,500° C. for re-graphitization. Although not required, the heattreatment temperature may be higher than 1,500° C. forre-graphitization, or may be in the range of from 1,500° C. to 2,500° C.A temperature higher than 2,500° C. may be used if so desired.

The starting materials for the preparation of graphene oxide gel includea graphitic material selected from natural graphite, artificialgraphite, meso-phase carbon, meso-phase pitch, meso-carbon micro-bead,soft carbon, hard carbon, coke, carbon fiber, carbon nano-fiber, carbonnano-tube, or a combination thereof.

The unitary graphene matrix composite shows a surprisingly high Rockwellhardness value, typically greater than 80 and often greater than 100.This is unprecedented since prior art flexible graphite foil, pyrolyticgraphite, or bulk graphite does not show such a high hardness.

The unitary graphene matrix composite of the present invention canexhibit an electrical conductivity greater than 1,500 S/cm, a thermalconductivity greater than 600 W/mK, a physical density greater than 1.8g/cm3, and/or a tensile strength greater than 80 MPa. With a higherre-graphitization temperature, the graphene monolithic can have anelectrical conductivity greater than 3,000 S/cm, a thermal conductivitygreater than 1,000 W/mK, a physical density greater than 1.9 g/cm3,and/or a tensile strength greater than 100 MPa. It can even exhibit anelectrical conductivity greater than 5,000 S/cm, a thermal conductivitygreater than 1,500 W/mK, a physical density greater than 2.0 g/cm³,and/or a tensile strength greater than 150 MPa.

Typically, the graphene oxide gel is prepared by immersing a graphiticmaterial in an oxidizing agent to form an initially optically opaquesuspension and allowing an oxidizing reaction to proceed until anoptically transparent or translucent solution is formed. The startinggraphitic material is selected from natural graphite, artificialgraphite, meso-phase carbon, meso-phase pitch, meso-carbon micro-bead,soft carbon, hard carbon, coke, carbon fiber, carbon nano-fiber, carbonnano-tube, or a combination thereof. The graphene oxide gel is composedof graphene oxide molecules dispersed in an acidic medium having a pHvalue of no higher than 5 and the graphene oxide molecules have anoxygen content no less than 20% by weight (typically from 20% toapproximately 46% by weight.

This graphene oxide gel has the characteristics that it is opticallytransparent or translucent and visually homogeneous with no discerniblediscrete graphene or graphene oxide sheets dispersed therein. Incontrast, conventional suspension of discrete graphene or graphene oxidesheets, or graphite flakes looks opaque, dark, black or heavy brown incolor with individual graphene sheets, graphene oxide sheets, orgraphite flakes being discernible or recognizable with naked eyes. Thegraphene oxide molecules dissolved in the liquid medium of a grapheneoxide gel are aromatic chains that have an average number of benzenerings in the chain typically less than 1000, more typically less than500, and most typically less than 100. Most of the molecules have morethan 5 or 6 benzene rings (mostly >10 benzene rings) from combinedatomic force microscopy, high-resolution TEM, and molecular weightmeasurements. These benzene-ring type of aromatic molecules have beenheavily oxidized and contain functional groups, such as —COOH and —OHand, therefore, are “soluble” (not just dispersible) in polar solvents,such as water.

These soluble molecules behave like resins and are surprisingly capableof forming a coherent layer of graphene oxide of good structuralintegrity and high thermal conductivity. By contrast, conventionaldiscrete graphene or graphene oxide sheets and graphite flakes do nothave any self-adhesion or cohesion power. These sheets or flakes wouldjust form a loosely packed mass of un-bonded particles that does nothave any structural integrity.

The present invention also provides a unitary graphene matrixcomposite-based heat spreader or heat sink product for use in ahand-held device, such as a power tool, a microelectronic ortelecommunication device (e.g. mobile phone, tablet, laptop computer,LCD display, etc), a light-emitting diode (LED) lighting device orsystem. The light weight (lower density compared to metal and ceramicmaterials), exceptional thermal conductivity, relatively high structuralintegrity, superior surface hardness and scratch resistance, andeliminated or significantly reduced tendency to emit free graphite orcarbon particles into air make the invented graphene oxide-coatedgraphitic layer an ideal thermal management material.

BRIEF DESCRIPTION OF THE DRAWINGS

-   -   FIG. 1(a) A flow chart illustrating various prior art processes        of producing exfoliated graphite products (flexible graphite        foils and flexible graphite composites) and pyrolytic graphite        (bottom portion), along with processes for producing graphene        oxide gel and GO gel-coated laminates;    -   FIG. 1(b) Schematic drawing illustrating the processes for        producing graphite or graphene oxide paper, mat, film, and        membrane of simply aggregated flakes/platelets. All processes        begin with intercalation and/or oxidation treatment of graphitic        materials (e.g. natural graphite particles).    -   FIG. 2(a) A SEM image of a graphite worm sample after thermal        exfoliation of graphite intercalation compounds (GICs) or        graphite oxide powders;    -   FIG. 2(b) An SEM image of a cross-section of a flexible graphite        foil, showing many graphite flakes with orientations not        parallel to the flexible graphite foil surface and also showing        many defects, kinked or folded flakes.    -   FIG. 3(a) A SEM image of a GO-derived graphene monolithic        wherein multiple graphene sheets, originally 30 nm-2 μm in        lateral dimension, have been oxidized, exfoliated, re-oriented,        and seamlessly merged into continuous-length graphene sheets or        layers that can run for hundreds of centimeters wide or long        (only a 120 μm or 0.12 mm width of a 25-cm wide unitary graphene        layer being shown in this SEM image);    -   FIG. 3(b) A SEM image of a cross-section of a graphene        paper/film prepared from discrete graphene sheets/platelets        using a paper-making process (e.g. vacuum-assisted filtration).        The image shows many discrete graphene sheets being folded or        interrupted (not integrated), with orientations not parallel to        the film/paper surface and having many defects or imperfections;    -   FIG. 3(c) Schematic drawing and an attendant SEM image to        illustrate the formation process of a unitary graphene entity or        graphene single crystal that is composed of multiple graphene        planes that are parallel to one another and are chemically        bonded in the thickness-direction or crystallographic c-axis        direction;    -   FIG. 3(d) Schematic of the prior art graphene poly-crystal        obtained by CVD of hydrocarbon on a catalytic surface (e.g. Cu        or Ni);    -   FIG. 3(e) Schematic of a graphene single crystal of the present        invention;    -   FIG. 3(f) Schematic of another graphene single crystal of the        present invention (a “poly-crystal” with incomplete grain        boundaries);    -   FIG. 3(g) One plausible chemical linking mechanism (only 2 GO        molecules are shown as an example; a large number of GO        molecules can be chemically linked together to form a unitary        graphene layer).    -   FIG. 4(a) Thermal conductivity values of the GO-derived single        unitary graphene layer (▴), GO paper (▪), and FG foil (♦)        plotted as a function of the final heat treatment temperature        for graphitization or re-graphitization;    -   FIG. 4(b) Thermal conductivity values of the GO-derived unitary        graphene layer (▪) and the polyimide-derived pyrolytic graphite        (PG) heat-treated for one hour (x) and for 3 hours (▴), all        plotted as a function of the final graphitization or        re-graphitization temperature;    -   FIG. 4(c) Electric conductivity values of the GO-derived unitary        graphene layer (♦), GO paper (▪), and FG foil (x) plotted as a        function of the final graphitization or re-graphitization        temperature;    -   FIG. 4(d) thermal conductivity values of unitary graphene layer        only, unitary graphene/CNT composite, GO paper (prepared from GO        platelets not reaching a GO gel state), and GO/CNT paper or        membrane;    -   FIG. 4(e) thermal conductivity values of unitary graphene layer        only, unitary graphene/CB composite, GO paper (prepared from GO        platelets not reaching a GO gel state), and GO/CB paper or        membrane. Note: symbol designations varied from (a) to (d).    -   FIG. 5(a) X-ray diffraction curves of a GO film,    -   FIG. 5(b) X-ray diffraction curve of GO film thermally reduced        at 150° C. (partially re-graphitized), and    -   FIG. 5(c) X-ray diffraction curve of highly reduced and        re-graphitized GO film (a unitary graphene layer).    -   FIG. 6(a) Inter-graphene plane spacing measured by X-ray        diffraction;    -   FIG. 6(b) the oxygen content in the GO-derived unitary graphene        layer; and    -   FIG. 6(c) thermal conductivity of GO-derived unitary graphene        layer and corresponding flexible graphite (FG) foil, all plotted        as a function of the final heat treatment temperature.    -   FIG. 7 Surface temperature fields of two identical smart phones        running the same video programs for 10 minutes. One smart phone        (top image) contains 2 sheets of flexible graphite (FG) foils        disposed between the CPU and the casing, showing an external        surface temperature as high as 38.6° C. The other smart phone        (bottom image) contains one sheet of unitary graphene        layer-coated FG foil, showing an external surface temperature of        25.4° C.    -   FIG. 8(a) Thermal conductivity values of the GO-derived unitary        graphene layer alone (▪), unitary graphene-expanded graphite        composite (♦, experimental values), expanded graphite foil alone        (exfoliated graphite worms broken up into separated graphite        flakes and re-compressed into foil) and FG foil alone (▴,        re-compressed worms without worm break-up and flake separation        as a point of reference) plotted as a function of the final        graphitization or re-graphitization temperature, along with        theoretically predicted values (x, unitary graphene-expanded        graphite composite) based on a rule-of-mixture law        (graphitization time=1 hour for all specimens);    -   FIG. 8(b) Thermal conductivity values of the GO-derived unitary        layer alone (▪), unitary graphene-expanded graphite composite        (♦), and polyimide-derived pyrolytic graphite (PG) plotted as a        function of the final graphitization or re-graphitization        temperature for one hour, along with those of PG graphitized for        3 hours.    -   FIG. 9(a) Tensile strength of unitary graphene matrix material        from GO gel, GO (not from gel state), and flexible graphite foil        over a range of heat treatment temperatures;    -   FIG. 9(b) Tensile strength and    -   FIG. 9(c) Rockwell hardness values of unitary graphene/CNT        composites, unitary graphene/expanded graphite composites, and        unitary graphene/carbon black composites plotted as a function        of the filler weight percentage, and    -   FIG. 9(d) Rockwell hardness of unitary graphene matrix material        only and its CNT-reinforced version plotted as a function of the        heat treatment temperature.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

The present invention provides a unitary graphene matrix compositecomprising: (a) a unitary graphene matrix containing closely packed andchemically bonded graphene planes having an inter-graphene plane spacingof 0.335 to 0.40 nm and an oxygen content of 0.001% to 10% by weight,which unitary graphene matrix is obtained from heat-treating a grapheneoxide gel at a temperature higher than 100° C. and contains no discretegraphene platelets derived from the graphene oxide gel; and (b) A carbonor graphite filler phase selected from a carbon or graphite fiber,carbon or graphite nano-fiber, carbon nano-tube, carbon nano-rod,meso-phase carbon particle, meso-carbon micro-bead, exfoliated graphiteflake with a thickness greater than 100 nm, exfoliated graphite orgraphite worm, coke particle, needle coke, carbon black or acetyleneblack particle, activated carbon particle, or a combination thereof. Thecarbon or graphite filler phase occupies a weight fraction of 0.01% to99% based on the total composite weight and the carbon or graphitefiller phase is preferably in a particulate, filamentary, or rod-likeform dispersed in the unitary graphene matrix. These discrete particles,filaments, and cylindrical shape fillers are the dispersed phase(reinforcement or filler phase) and the GO-derived unitary graphenematerial is the continuous phase (matrix).

Preferably and typically, most of the chemically bonded graphene planesin the unitary graphene matrix are parallel to one another. The unitarygraphene matrix is often a graphene single crystal or a graphenepoly-crystal that contains no complete grain boundary therein.Typically, the carbon or graphite filler is chemically bonded by theunitary graphene matrix material. This chemical bonding is morepronounced if the carbon/graphite filler is chemically treated (e.g.using a mixture of sulfuric acid and nitric acid) prior to being mixedwith the GO gel.

The heat treatment temperature conditions are such that the unitarygraphene matrix composite is relatively pore-free having a physicaldensity of at least 1.5 g/cm³ or a porosity level lower than 20%. Undermore typical processing conditions, the unitary graphene matrixcomposite has a physical density of at least 1.7 g/cm³ or a porositylevel lower than 10%. In most cases, the unitary graphene matrixcomposite has a physical density greater than 1.8 g/cm³ or a porositylevel less than 5%. The chemically bonded graphene planes in the unitarygraphene composite typically contain a combination of sp² and sp³electronic configurations.

In a preferred embodiment of the present invention, the process forproducing the unitary graphene matrix composite comprises: (a) preparinga graphene oxide gel having graphene oxide molecules dispersed in afluid medium, wherein the graphene oxide gel is optically transparent ortranslucent; (b) mixing the carbon or graphite filler phase in thegraphene oxide gel to form a slurry; (c) dispensing the slurry onto asurface of a supporting substrate or a cavity of a molding tool; (d)partially or completely removing the fluid medium from the slurry toform a composite precursor; and (e) heat-treating the compositeprecursor to form the unitary graphene composite at a temperature higherthan 100° C. (preferably >500° C. and more preferably from 500° C. to1500° C.). Although not required, higher temperatures may be used if sodesired.

In this process, steps (c) and (d) preferably include feeding a sheet ofa solid substrate material from a roller to a deposition zone,dispensing the slurry or suspension onto a surface of the sheet of solidsubstrate material to form a slurry layer thereon, drying the slurry orsuspension to form a dried composite precursor layer deposited on thesubstrate surface, and collecting composite precursor-depositedsubstrate sheet on a collector roller. The process may further comprisea step of compressing the composite precursor prior to being collectedon the collector roller. This makes a roll-to-roll process amenable tomass production of graphene matrix composites.

Alternatively, the process may comprise: (a) preparing a graphene oxidegel having graphene oxide molecules dispersed in a fluid medium, whereinthe graphene oxide gel is optically transparent or translucent; (b)forming the carbon or graphite filler phase into a desired porous shapehaving pores therein, and impregnating the graphene oxide gel into thesepores of the desired porous shape to form an impregnated shape; (c)partially or completely removing the fluid medium from the impregnatedshape to form a composite precursor; and (d) heat-treating the compositeprecursor to form the unitary graphene composite at a temperature higherthan 100° C. Again, the re-graphitization temperature ispreferably >500° C. and more preferably from 500° C. to 1500° C.Although not required, higher heat treatment temperatures may be used ifso desired. The desired porous shape may be a porous woven fabric,porous non-woven fabric, porous mat, or porous paper.

In yet another preferred embodiment, the process for producing theunitary graphene matrix composite comprises: (a) preparing a grapheneoxide gel having graphene oxide molecules dispersed in a fluid medium,wherein the graphene oxide gel is optically transparent or translucent;(b) combining the carbon or graphite filler phase and the graphene oxidegel to form a graphene oxide gel-impregnated shape of fiber yarns orbundles; (c) partially or completely removing the fluid medium fromgraphene oxide gel-impregnated shape to form a composite precursor; and(d) heat-treating the composite precursor to form the unitary graphenecomposite at a temperature higher than 100° C. The graphene oxidegel-impregnated shape may be selected from a unidirectional,bi-directional, multi-directional, angle-plied, woven, or filament-woundshape. In other words, the processes for producing conventional resinmatrix composites, such as filament winding, pultrusion, yarn weaving,and pre-impregnating, may be adapted to fabricate the graphene matrixcomposite.

This is quite surprising for several reasons: (1) The GO gel andconventional polymer melts or polymer-solvent solutions appear toexhibit very different and distinct rheological behaviors; (2) It iswell-known in the field of polymer science that highly aromatic chainsare typically not soluble, melt-able, or flowable to enable solution ormelt processing and GO molecules are highly aromatic; (3) Much to thesurprise of polymer scientists, heavy oxidation can chemically convertdiscrete solid graphite flakes to soluble GO molecules and these highlyaromatic molecules can be chemically linked together to form huge 2Dgiant molecules or 3D network of “cross-linked” graphene chains thatprovide cohesiveness and adhesiveness required of a resin matrixcomposite having a good resin-filler interfacial bonding.

The graphene oxide gel may be prepared by immersing a graphitic materialin a powder or fibrous form in an oxidizing liquid to form an initiallyoptically opaque suspension in a reaction vessel at a reactiontemperature for a length of time sufficient to obtain a graphene oxidegel that is optically transparent or translucent. The graphene oxide gelis composed of graphene oxide molecules dispersed in an acidic mediumhaving a typical pH value of no higher than 5 and the graphene oxidemolecules have an oxygen content typically no less than 20% by weightwhen the system is in a gel state.

Specifically, a graphitic material may be immersed in an oxidizing agentto form an optically opaque suspension. It is initially opaque becausethe starting graphitic material is in a carbon or graphite particulateform having a particle size or chemical nature that scatters visiblewavelength or absorbs light. Useful starting materials include naturalgraphite, artificial graphite, meso-phase carbon, meso-phase pitch,meso-carbon micro-bead, soft carbon, hard carbon, coke, carbon fiber,carbon nano-fiber, carbon nano-tube, or a combination thereof. As theoxidizing reaction proceeds to a critical extent, an opticallytransparent or translucent solution is formed.

All the aforementioned processes may further comprise a step ofcompressing the composite precursor prior to or during heat treating.Preferably, the processing conditions involve a shear stress field thatpromotes alignment of GO molecules.

The graphene oxide (GO) gel-derived unitary graphene material and theunitary graphene matrix composite have the following characteristics(separately or in combination):

-   -   (1) The unitary graphene matrix material, alone or with a filler        phase, is an integrated graphene phase that is either a graphene        single crystal or a poly-crystal having multiple grains with        incomplete grain boundaries. When made into a thin film (e.g.        <200 μm) under a desired shearing stress field condition, both        the unitary graphene matrix alone or the corresponding graphene        matrix composite have wide/long chemically bonded graphene        planes that are essentially oriented parallel to one another. In        other words, the crystallographic c-axis directions of all        grains and all their constituent graphene planes are essentially        pointing in the same direction. It may be noted that the grains        in a graphene poly-crystal have very poorly delineated or        incomplete grain boundaries. These grains are essentially a        single grain with some residual demarcation lines (e.g., FIG.        3(f)). Such type of graphene poly-crystal is best described as a        graphene single crystal with some aligned but sporadic defects.        This conclusion was drawn after an extensive investigation using        a combination of SEM, TEM, selected area diffraction (with a        TEM), X-ray diffraction, atomic force microscopy (AFM), Raman        spectroscopy, and FTIR.    -   (2) The paper-like sheets of exfoliated graphite worms (i.e.,        flexible graphite foils), mats of expanded graphite flakes (100        nm in thickness), and paper or membrane of graphene or GO        platelets are a simple, un-bonded aggregate/stack of multiple        discrete graphite flakes or discrete platelets of graphene, GO,        or RGO. In contrast, the unitary graphene matrix of the present        invention is a fully integrated, single graphene entity or        monolith containing no discrete flakes or platelets derived from        the GO gel.    -   (3) In prior art processes, discrete graphene sheets (<<100 nm)        or expanded graphite flakes (>100 nm) that constitute the        original structure of graphite particles could be obtained via        expanding, exfoliating, and separating treatments. By simply        mixing and re-compressing these discrete sheets/flakes into a        thin film, one could attempt to orient these sheets/flakes        hopefully along one direction. However, with these conventional        processes, the constituent flakes or sheets of the resulting        film (aggregate, paper, membrane, or mat) would remain as        discrete flakes/sheets/platelets that can be easily discerned or        clearly observed even with an un-assisted eye or under a        low-magnification optical microscope (×100-×1000).        -   In contrast, the preparation of the presently invented            unitary graphene structure involves heavily oxidizing the            original graphite particles, to the extent that practically            every one of the original graphene planes has been oxidized            and isolated from one another to become individual molecules            that possess highly reactive functional groups (e.g. —OH and            —COOH) at the edge and, mostly, on graphene planes as well.            These individual hydrocarbon molecules (containing elements            such as O and H, in addition to carbon atoms) are dissolved            in the reaction medium (e.g. mixture of water and acids) to            form a gel-like mass, herein referred to as the GO gel. This            gel is then cast onto a smooth substrate surface or injected            into a mold cavity, typically under shear stress field            conditions, and the liquid components are then removed to            form a dried GO layer. When heated, these highly reactive            molecules react and chemically join with one another mostly            in lateral directions along graphene planes (in an            edge-to-edge manner) and, in some cases, between graphene            planes as well.        -   Illustrated in FIG. 3(g) is a plausible chemical linking            mechanism where only 2 aligned GO molecules are shown as an            example, although a large number of GO molecules can be            chemically linked together to form a unitary graphene layer.            Further, chemical linking could also occur face-to-face, not            just edge-to-edge. These linking and merging reactions            proceed in such a manner that the molecules are chemically            merged, linked, and integrated into one single entity or            monolith. The molecules completely lose their own original            identity and they no longer are discrete            sheets/platelets/flakes. There is only one single layer-like            structure (unitary graphene entity) that is one huge            molecule or just a network of interconnected giant molecules            with an essentially infinite molecular weight. This may also            be described as a graphene single crystal (with only one            grain in the entire structure or entity, or a poly-crystal            (with several grains, but typically no discernible,            well-defined grain boundaries). All the constituent graphene            planes are very large in lateral dimensions (length and            width) and, if produced under shear stress conditions            (particularly into thin films, <200 μm in thickness) and            heat-treated at a higher temperature (e.g. >700° C. or much            higher), these graphene planes are essentially parallel to            one another.        -   In-depth studies using a combination of SEM, TEM, selected            area diffraction , X-ray diffraction, AFM, Raman            spectroscopy, and FTIR indicate that the graphene monolith            is composed of several huge graphene planes (with            length/width typically >>100 μm, more typically >>1 mm, and            most typically >>1 cm). These giant graphene planes are            stacked and bonded along the thickness direction            (crystallographic c-axis direction) often through not just            the van der Waals forces (as in conventional graphite            crystallites), but also covalent bonds, Not to be limited by            theory, but Raman and FTIR spectroscopy studies appear to            indicate the co-existence of sp² (dominating) and sp³ (weak            but existing) electronic configurations, not just the            conventional sp² in graphite.    -   (4) This integrated graphene entity is not made by gluing or        bonding discrete flakes/platelets together with a resin binder,        linker, or adhesive. Instead, GO molecules in the GO gel are        merged through joining or forming of covalent bonds with one        another, into an integrated graphene entity, without using any        externally added linker or binder molecules or polymers.    -   (5) This unitary or monolithic graphene entity is a single        crystal (e.g. FIG. 3(e)) or poly-crystal (having incomplete        grain boundaries, FIG. 3(f)), typically with the        crystallographic c-axis in all grains being essentially parallel        to each other. This entity is derived from a GO gel, which is in        turn obtained from natural graphite or artificial graphite        particles originally having multiple graphite crystallites.        Prior to being chemically oxidized, these starting graphite        crystallites have an initial length (L_(a) in the        crystallographic α-axis direction), initial width (L_(b) in the        b-axis direction), and thickness (L_(c) in the c-axis        direction). Upon heavy oxidation, these initially discrete        graphite particles are chemically transformed into highly        aromatic graphene oxide molecules having a significant        concentration of edge- or surface-borne functional groups (e.g.        —OH, —COOH, etc.). These aromatic GO molecules in the GO gel        have lost their original identity of being part of a graphite        particle or flake. Upon removal of the liquid component from the        GO gel, the resulting GO molecules form an essentially amorphous        structure. Upon heat treatment (re-graphitization treatment),        these GO molecules are chemically merged and linked into a        unitary or monolithic graphene entity that is highly ordered        (essentially a single crystal).        -   The resulting unitary graphene entity typically has a length            or width significantly greater than the L_(a) and L_(b) of            the original crystallites. The length/width of this unitary            graphene entity or that of a graphene single crystal is            typically greater than the L_(a) and L_(b) of the original            crystallites. Even the individual grains in a            poly-crystalline unitary graphene entity have a length or            width significantly greater than the L_(a) and L_(b) of the            original crystallites. They can be as large as the length or            width of the unitary graphene entity itself, not just 2 or 3            times higher than the initial L_(a) and L_(b) of the            original crystallites.    -   (6) Due to these unique chemical composition (including oxygen        content), morphology, crystal structure (including        inter-graphene spacing), and structural features (e.g. defects,        incomplete or lack of grain boundaries, chemical bonding and no        gap between graphene sheets, and no interruptions in graphene        planes), the graphene oxide gel-derived unitary or monolithic        graphene layer has a unique combination of outstanding thermal        conductivity, electrical conductivity, mechanical strength, and        scratch resistance (including elimination of the tendency for        surface graphite flakes or particles to “flake off” since there        is essentially no GO gel-derived discrete flake or platelet in        this graphene monolith structure). Even in a unitary graphene        matrix composite containing expanded graphite flakes, these        flakes are essentially embraced and bonded with an integrated        graphene film, allowing no exposed flakes.

The aforementioned features are further described and explained indetails as follows:

As illustrated in FIG. 1(b), a graphite particle (e.g. 100) is typicallycomposed of multiple graphite crystallites or grains. A graphitecrystallite is made up of layer planes of hexagonal networks of carbonatoms. These layer planes of hexagonally arranged carbon atoms aresubstantially flat and are oriented or ordered so as to be substantiallyparallel and equidistant to one another in a particular crystallite.These layers of carbon atoms, commonly referred to as graphene layers orbasal planes, are weakly bonded together in their thickness direction(crystallographic c-axis direction) by weak van der Waals forces andgroups of these graphene layers are arranged in crystallites.

The graphite crystallite structure is usually characterized in terms oftwo axes or directions: the c-axis direction and the α-axis (or b-axis)direction. The c-axis is the direction perpendicular to the basalplanes. The α- or b-axes are the directions parallel to the basal planes(perpendicular to the c-axis direction).

A highly ordered graphite particle can consist of crystallites of aconsiderable size, having a length of L_(a) along the crystallographicα-axis direction, a width of L_(b) along the crystallographic b-axisdirection, and a thickness L_(c) along the crystallographic c-axisdirection. The constituent graphene planes of a crystallite are highlyaligned or oriented with respect to each other and, hence, theseanisotropic structures give rise to many properties that are highlydirectional. For instance, the thermal and electrical conductivity of acrystallite are of great magnitude along the plane directions (α- orb-axis directions), but relatively low in the perpendicular direction(c-axis). As illustrated in the upper-left portion of FIG. 1(b),different crystallites in a graphite particle are typically oriented indifferent directions and, hence, a particular property of amulti-crystallite graphite particle is the directional average value ofall the constituent crystallites.

Due to the weak van der Waals forces holding the parallel graphenelayers, natural graphite can be treated so that the spacing between thegraphene layers can be appreciably opened up so as to provide a markedexpansion in the c-axis direction, and thus form an expanded graphitestructure in which the laminar character of the carbon layers issubstantially retained. The process for manufacturing flexible graphiteis well-known and the typical practice is described in U.S. Pat. No.3,404,061 to Shane et al., the disclosure of which is incorporatedherein by reference. In general, flakes of natural graphite (e.g. 100 inFIG. 1(b)) are intercalated in an acid solution to produce graphiteintercalation compounds (GICs, 102). The GICs are washed, dried, andthen exfoliated by exposure to a high temperature for a short period oftime. This causes the flakes to expand or exfoliate in the c-axisdirection of the graphite up to 80-300 times of their originaldimensions. The exfoliated graphite flakes are vermiform in appearanceand, hence, are commonly referred to as worms 104. These worms ofgraphite flakes which have been greatly expanded can be formed withoutthe use of a binder into cohesive or integrated sheets of expandedgraphite, e.g. webs, papers, strips, tapes, foils, mats or the like(typically referred to as “flexible graphite” 106) having a typicaldensity of about 0.04-2.0 g/cm³ for most applications.

The upper left portion of FIG. 1(a) shows a flow chart that illustratesthe prior art processes used to fabricate flexible graphite foils andthe resin-impregnated flexible graphite composite. The processestypically begin with intercalating graphite particles 20 (e.g., naturalgraphite or synthetic graphite) with an intercalant (typically a strongacid or acid mixture) to obtain a graphite intercalation compound 22(GIC). After rinsing in water to remove excess acid, the GIC becomes“expandable graphite.” The GIC or expandable graphite is then exposed toa high temperature environment (e.g., in a tube furnace preset at atemperature in the range of 800-1,050° C.) for a short duration of time(typically from 15 seconds to 2 minutes). This thermal treatment allowsthe graphite to expand in its c-axis direction by a factor of 30 toseveral hundreds to obtain a worm-like vermicular structure 24 (graphiteworm), which contains exfoliated, but un-separated graphite flakes withlarge pores interposed between these interconnected flakes. An exampleof graphite worms is presented in FIG. 2(a).

In one prior art process, the exfoliated graphite (or mass of graphiteworms) is re-compressed by using a calendering or roll-pressingtechnique to obtain flexible graphite foils (26 in FIG. 1(a) or 106 inFIG. 1(b)), which are typically much thicker than 100 μm. An SEM imageof a cross-section of a flexible graphite foil is presented in FIG.2(b), which shows many graphite flakes with orientations not parallel tothe flexible graphite foil surface and there are many defects andimperfections.

Largely due to these mis-orientations of graphite flakes and thepresence of defects, commercially available flexible graphite foilsnormally have an in-plane electrical conductivity of 1,000-3,000 S/cm,through-plane (thickness-direction or Z-direction) electricalconductivity of 15-30 S/cm, in-plane thermal conductivity of 140-300W/mK, and through-plane thermal conductivity of approximately 10-30W/mK. These defects and mis-orientations are also responsible for thelow mechanical strength (e.g. defects are potential stress concentrationsites where cracks are preferentially initiated). These properties areinadequate for many thermal management applications and the presentinvention is made to address these issues.

In another prior art process, the exfoliated graphite worm 24 may beimpregnated with a resin and then compressed and cured to form aflexible graphite composite 28, which is normally of low strength aswell. In addition, upon resin impregnation, the electrical and thermalconductivity of the graphite worms could be reduced by two orders ofmagnitude.

Alternatively, the exfoliated graphite may be subjected tohigh-intensity mechanical shearing/separation treatments using ahigh-intensity air jet mill, high-intensity ball mill, or ultrasonicdevice to produce separated nano graphene platelets 33 (NGPs) with allthe graphene platelets thinner than 100 nm, mostly thinner than 10 nm,and, in many cases, being single-layer graphene (also illustrated as 112in FIG. 1(b). An NGP is composed of a graphene sheet or a plurality ofgraphene sheets with each sheet being a two-dimensional, hexagonalstructure of carbon atoms.

Further alternatively, with a low-intensity shearing, graphite wormstend to be separated into the so-called expanded graphite flakes (108 inFIG. 1(b) having a thickness >100 nm. These flakes can be formed intographite paper or mat 110 using a paper- or mat-making process. Thisexpanded graphite paper or mat 110 is just a simple aggregate or stackof discrete flakes having defects, interruptions, and mis-orientationsbetween these discrete flakes.

For the purpose of defining the geometry and orientation of an NGP, theNGP is described as having a length (the largest dimension), a width(the second largest dimension), and a thickness. The thickness is thesmallest dimension, which is no greater than 100 nm, preferably smallerthan 10 nm in the present application. When the platelet isapproximately circular in shape, the length and width are referred to asdiameter. In the presently defined NGPs, both the length and width canbe smaller than 1 μm, but can be larger than 200 μm.

A mass of multiple NGPs (including single-layer and/or few-layergraphene sheets, 33 in FIG. 1(a)) may be made into a graphene film/paper(34 in FIG. 1(a) or 114 in FIG. 1(b)) using a film- or paper-makingprocess. FIG. 3(b) shows a SEM image of a cross-section of a graphenepaper/film prepared from discrete graphene sheets using a paper-makingprocess. The image shows the presence of many discrete graphene sheetsbeing folded or interrupted (not integrated), most of plateletorientations being not parallel to the film/paper surface, the existenceof many defects or imperfections. NGP aggregates, even when beingclosely packed, exhibit a thermal conductivity higher than 1,000 W/mKonly when the film or paper is cast and strongly pressed into a sheethaving a thickness lower than 10 μm, and higher than 1,500 W/mK onlywhen the film or paper is cast and pressed into a sheet having athickness lower than 1 μm. A heat spreader in many electronic devices isnormally required to be thicker than 25 μm and, more desirably, thickerthan 50 μm based mainly on handling ease and structural integrityconsiderations (but no greater than 200 μm due to device volumeconstraint).

The precursor to the unitary graphene layer is graphene oxide gel. ThisGO gel is obtained by immersing a graphitic material 20 in a powder orfibrous form in a strong oxidizing liquid in a reaction vessel to form asuspension or slurry, which initially is optically opaque. This opticalopacity reflects the fact that, at the outset of the oxidizing reaction,the discrete graphite flakes and, at a later stage, the discretegraphene oxide flakes scatter and/or absorb visible wavelengths,resulting in an opaque and generally dark fluid mass. If the reactionbetween graphite powder and the oxidizing agent is allowed to proceed ata sufficiently high reaction temperature for a sufficient length oftime, this opaque suspension is transformed into a translucent ortransparent solution, which is now a homogeneous fluid called “grapheneoxide gel” (21 in FIG. 1(a)) that contains no discernible discretegraphite flakes or graphite oxide platelets.

Again, this graphene oxide gel is optically transparent or translucentand visually homogeneous with no discernible discrete flakes/plateletsof graphite, graphene, or graphene oxide dispersed therein. In contrast,conventional suspension of discrete graphene sheets, graphene oxidesheets, and expanded graphite flakes in a fluid (e.g. water, organicacid or solvent) look dark, black or heavy brown in color withindividual graphene or graphene oxide sheets or expanded graphite flakesdiscernible or recognizable even with naked eyes or a low-magnificationlight microscope (100×-1,000×).

The graphene oxide molecules dissolved in the liquid medium of agraphene oxide gel are aromatic chains that have an average number ofbenzene rings in the chain typically less than 1,000, more typicallyless than 500, and many less than 100. Most of the molecules have morethan 5 or 6 benzene rings (mostly >10 benzene rings) from combinedatomic force microscopy, high-resolution TEM, and molecular weightmeasurements. Based on our elemental analysis, these benzene-ring typeof aromatic molecules are heavily oxidized, containing a highconcentration of functional groups, such as —COOH and —OH and,therefore, are “soluble” (not just dispersible) in polar solvents, suchas water. The estimated molecular weight of these graphene oxidepolymers in the gel state is typically between 200 g/mole and 43,000g/mole, more typically between 400 g/mole and 21,500 g/mole, and mosttypically between 400 g/mole and 4,000 g/mole.

These soluble molecules behave like polymers and are surprisinglycapable of reacting and getting chemically connected with one another(during the subsequent heat treatment or re-graphitization treatment) toform a unitary graphene layer of good structural integrity and highthermal conductivity. Conventional discrete graphene sheets, grapheneoxide sheets, or graphite flakes do not have any self-reacting orcohesive bonding capability. Also very surprisingly, during thesubsequent heat treatment or re-graphitization treatment, these solublemolecules in the GO gel are capable of chemically bonding a carbon orgraphite filler phase (e.g. carbon fibers, expanded graphite flakes,CNTs, carbon black particles, etc.) dispersed in the GO gel.

Again, specifically and most significantly, these graphene oxidemolecules present in a GO gel state are capable of chemically mergingwith one another and getting integrated into extremely long and widegraphene layers (e.g. FIG. 3(a)) when the gel is dried and heat-treatedat a sufficiently high temperature for a sufficiently long period oftime. These graphene layers can run as wide as the specimen width itself(up to hundreds of centimeters) that are parallel to one another. Noindividual graphene platelets or sheets are discernible; they have beenfully linked and integrated chemically with one another to form alayer-like unitary body in the graphene plane direction and theseunitary bodies appear to be chemically bonded with one another along thethickness-direction (or Z-direction). X-ray diffraction studies haveconfirmed that the d-spacing (inter-graphene plane distance) has beenrecovered back to approximately 0.335 nm (with <0.02% by weight ofoxygen) to 0.40 nm (with approximately 5.0-10% oxygen). There does notappear to be any gap between these graphene layers and, hence, theselayers have been essentially merged into one big unitary body, which isa graphene single crystal. FIG. 3(a) depicts an example of such a hugeunitary body. Although there appears to be some demarcations betweenunitary layers, these perceived demarcations are due to slightlydifferent widths between layers. Each layer is composed of one ofmultiple graphene planes parallel to one another. These seeminglyindividual unitary layers actually have formed into a single integratedentity or a graphene single crystal. The formation process for such agraphene single crystal is further illustrated in FIG. 3(c).

It may be noted that the presently invented graphene single crystal isfundamentally different and patently distinct from the catalytic CVDgraphene thin film in terms of chemical composition, micro-structure,morphology, process of production, all chemical and physical properties,and intended applications. This is explained as follows:

-   -   (a) As schematically shown in FIG. 3(d), the prior art graphene        poly-crystal obtained by CVD of hydrocarbon on a catalytic        surface (e.g. Cu or Ni) is typically composed of many grains        with grain size typically smaller than 10 μm (most often <5 μm).        These grains also have different orientations with respect to        one another.    -   (b) In contrast, FIG. 3(e) shows a schematic of a graphene        single crystal of the present invention having just one single        grain or domain. There are no grain boundaries that can impede        the movement of electrons or phonons and, hence, this        single-grain single crystal has an exceptionally high electrical        conductivity and thermal conductivity.    -   (c) FIG. 3(f) shows a schematic of another graphene single        crystal of the present invention, which is a “poly-crystal” with        incomplete grain boundaries. The graphene planes in all the        grains are oriented parallel to one another.    -   (d) The presently invented graphene single crystal from GO gel        typically has an oxygen content from 0.01% to 5%, but no        hydrogen (H). In contrast, the catalytic CVD graphene film has        some hydrogen content, but no oxygen.    -   (e) Typically, the CVD graphene film grown on Cu or Ni surface        is single layer or inhomogeneous few-layer graphene with a        thickness less than 2 nm (the underlying Cu or Ni foil is not        capable of providing catalytic effect when the deposited carbon        layer exceeds 2 nm). These ultra-thin layers are thus optically        transparent and are intended for touch panel screen applications        to replace the ITO glass. In contrast, our graphene monolith is        typically thicker than 10 nm (more typically thicker than 1 μm,        and most typically thicker than 10 μm) and, hence, typically is        optically opaque. The graphene monolith of the present invention        has a significantly higher thermal conductivity and can be more        easily handled when being implemented into an electronic device        (e.g. a mobile phone) as a heat spreader.

The unitary graphene layer can be used alone as a heat spreader in anelectronic device. Alternatively, this unitary graphene layer can be amatrix material for a composite containing a carbon or graphite filler(e.g. meso-phase carbon particles, carbon black, acetylene black, needlecoke, expanded graphite flake, carbon fiber, CNT, etc). This unitarygraphene material is the matrix or dispersing phase, not the filler ordispersed phase, in this unique and novel “graphene matrix composite.”This is in sharp contrast to all the prior art graphene composites (orgraphene-reinforced composites) wherein discrete graphene platelets arethe dispersed phase (reinforcement or filler phase) that is dispersed inor bonded by a matrix phase (e.g. resin, glass, metal, or ceramicmatrix). These prior art composites are in fact graphene-reinforcedresin matrix, glass matrix, metal matrix, or ceramic matrix composite.They are not the graphene matrix composite of the present invention.

The unitary graphene matrix composite preferably has a thickness nogreater than 1 mm, further preferably less than 200 μm, and mostpreferably less than 100 μm. More preferably, the thickness is greaterthan 10 μm, further preferably between 10 and 100 μm.

The graphene oxide is obtained from a graphene oxide gel, which gel iscomposed of graphene oxide molecules dispersed in an acidic mediumhaving a pH value of no higher than 5 and the graphene oxide moleculeshave an oxygen content no less than 20% by weight (typically between 20and 46%). In particular, the gel is obtained by immersing a graphiticmaterial in a powder or fibrous form in an oxidizing liquid in areaction vessel at a reaction temperature for a length of timesufficient to obtain a graphene oxide gel composed of graphene oxidemolecules dispersed in an acidic liquid medium having a pH value of nohigher than 5 and the graphene oxide molecules have an oxygen content noless than 20% by weight. The subsequent heat treatment process naturallyreduces the oxygen content to typically 0.01-10% by weight, moretypically 0.01%-5%.

The starting graphitic material to be heavily oxidized for the purposeof forming graphene oxide gel may be selected from natural graphite,artificial graphite, meso-phase carbon, meso-phase pitch, meso-carbonmicro-bead, soft carbon, hard carbon, coke, carbon fiber, carbonnano-fiber, carbon nano-tube, or a combination thereof. The graphiticmaterial is preferably in a powder or short filament form having adimension lower than 20 μm, more preferably lower than 10 μm, furtherpreferably smaller than 5 μm, and most preferably smaller than 1 μm.

Using artificial graphite with an average particle size of 9.7 μm as anexample, a typical procedure involves dispersing graphite particles inan oxidizer mixture of sulfuric acid, nitric acid, and potassiumpermanganate (at a weight ratio of 3:1:0.05) at a temperature oftypically 0-60° C. for typically at least 3 days, preferably 5 days, andmore preferably 7 days or longer. The average molecular weight of theresulting graphene oxide molecules in a gel is approximately20,000-40,000 g/mole if the treatment time is 3 days, <10,000 g/mole if5 days, and <4,000 g/mole if longer than 7 days. The required gelformation time is dependent upon the particle size of the originalgraphitic material, a smaller size requiring a shorter time. It is offundamental significance to note that if the critical gel formation timeis not reached, the suspension of graphite powder and oxidizer (graphiteparticles dispersed in the oxidizer liquid) appears completely opaque,meaning that discrete graphite particles or flakes remain suspended (butnot dissolved) in the liquid medium. As soon as this critical time isexceeded, the whole suspension becomes optically translucent ortransparent, meaning that the heavily oxidized graphite completely losesits original graphite identity and the resulting graphene oxidemolecules are completely dissolved in the oxidizer liquid, forming ahomogeneous solution (no longer just a suspension or slurry).

It must be further noted that if the suspension or slurry, with atreatment time being shorter than the required gel formation time, isrinsed and dried, we would simply recover a graphite oxide powder orgraphite intercalation compound (GIC) powder, which can be exfoliatedand separated to produce nano graphene platelets (NGPs). Without anadequate amount of a strong oxidizing agent and an adequate duration ofoxidation time, the graphite or graphite oxide particles would not beconverted into the GO gel state.

The filler or reinforcement phase in the unitary graphene matrixcomposite may be selected from particles of fine natural graphite,artificial graphite, expanded graphite, meso-phase carbon, meso-phasepitch, meso-carbon micro-bead, soft carbon, hard carbon, coke, carbonfiber, carbon nano-fiber, carbon nano-tube, or a combination thereof.

The graphene oxide-derived unitary graphene matrix composite containinga carbon or graphite filler phase of the present invention typically hasa thermal conductivity greater than 800 W/mK, more typically greaterthan 1,000 W/mK (even when the film thickness is greater than 10 μm) andoften greater than 1,700 W/mK. This latter valve is typically obtainedwhen the carbon/graphite filler is exfoliated graphite flakes (>100 nm,but preferably <500 nm) or pristine graphene platelets (<100 nm,preferably <10 nm) and when the final heat treatment temperature ishigher than 2,500° C. The graphene matrix composite typically has anelectrical conductivity greater than 3,000 S/cm (even >10,000 S/cm).This high electrical conductivity (greater than 3000 S/cm and up to15,000 S/cm) can be achieved concurrently with a thermal conductivitygreater than 1,000 W/mK (up to 1,800 W/mK). Quite often, the unitarygraphene matrix composite can exhibit a combination of a high electricalconductivity (greater than 1,500 S/cm, more often >3,000 S/cm), a highthermal conductivity (greater than 600 W/mK, more often greater than 800W/mK), a relatively high physical density (greater than 1.8 g/cm³), anda relatively high tensile strength (greater than 40 MPa, often >80 MPa,and can be >120 MPa). Unidirectional carbon fiber reinforced graphenematrix composites can exhibit a tensile strength significantly higherthan 200 MPa. The unitary graphene matrix composite also exhibits anexceptional surface hardness and scratch resistance, eliminating thetendency to flake off (to emit free carbon or graphite particles intoair) which has been a serious problem associated with the flexiblegraphite foil and the recompressed graphene platelet foil.

The unitary graphene matrix of the present invention is often a singlecrystal (as schematically shown in FIG. 3(e)) or a poly-crystal withincomplete grain boundaries (e.g. schematically shown in FIG. 3(f))which is essentially a graphene single crystal as well. By contrast, theprior art graphene film (single layer or few layer <2 nm thick) preparedby catalytic chemical vapor deposition (CVD) on a catalyst surface (Cuor Ni) is essentially poly-crystalline graphene with grain sizestypically <100 μm and more typically <10 μm. This CVD graphene film isintended for use as a semiconductor material (e.g. to replace Si in aFET transistor) or as a touch panel screen (e.g. to replace ITO glassused in a display device such as mobile phone screen). This CVD grapheneis made by catalyst-assisted decomposition of hydrocarbon gas moleculesand deposition of resulting carbon atoms on a Cu or Ni foil at a CVDtemperature of typically 800-1,000° C. The electrical conductivity(<1,000 S/cm) and thermal conductivity (<500 W/mK) of the CVD graphenefilms are typically significantly lower than those of the presentlyinvented graphene single crystals even though these CVD films aretypically thinner than 2 nm and our graphene single crystals aretypically thicker than 10 nm (often thicker than 10 μm).

As indicated above, flexible graphite foils prepared by re-compressionof exfoliated graphite flakes or graphite worms exhibit relatively lowthermal conductivity and mechanical strength. The graphite worms can beformed into flexible graphite foils by compression, without the use ofany binding material, presumably due to the mechanical interlockingbetween the voluminously expanded graphite flakes. Although asignificant proportion of these flakes are oriented in a directionlargely parallel to the opposing surfaces of a flexible graphite sheet(as evidenced by the high degree of anisotropy with respect to thermaland electrical conductivity), many other flakes are distorted, kinked,bent over, or oriented in a direction non-parallel to these sheetsurfaces (FIG. 2(b)). This observation has been well demonstrated inmany scanning electron micrographs (SEM) published in open or patentliterature. Furthermore, the presence of a large number of graphiteflakes implies a large amount of interface between flakes, resulting invery high contact resistance (both thermal and electrical resistance).

As a consequence, the electrical or thermal conductivity of theresulting flexible graphite foils dramatically deviates from what wouldbe expected of a perfect graphite single crystal or a graphene layer.For instance, the theoretical in-plane electrical conductivity andthermal conductivity of a graphene layer are predicted to be 1-5×10⁴S/cm and 3,000-5,000 W/(mK), respectively. However, the actualcorresponding values for flexible graphite foils are 1-3×10³ S/cm and140-300 W/(mK), respectively; one order of magnitude lower than whatcould be achieved. By contrast, the corresponding values for thepresently invented unitary graphene matrix composite containingseparated expanded graphite flakes are approximately 3.5-20×10³ S/cm(3,500-20,000 S/cm) and 600-1,800 W/(mK), respectively.

As a preferred embodiment of the present invention, the unitary graphenematrix composite comprises (a) a unitary graphene matrix containinggraphene planes having an inter-graphene plane spacing of 0.335 to 0.40nm and an oxygen content less than 1% by weight, which unitary graphenematrix is obtained from heat-treating a graphene oxide gel at atemperature higher than 500° C. and contains no discrete grapheneplatelets derived from the graphene oxide gel; (b) a carbon or graphitefiller phase selected from a carbon or graphite fiber, carbon orgraphite nano-fiber, carbon nano-tube, carbon nano-rod, meso-phasecarbon particle, meso-carbon micro-bead, exfoliated graphite flake witha thickness greater than 100 nm, exfoliated graphite or graphite worm,coke particle, needle coke, carbon black or acetylene black particle,activated carbon particle, or a combination thereof. The carbon orgraphite filler phase occupies a weight fraction from 1% to 90% based onthe total composite weight and the carbon or graphite filler phase ispreferably in a particulate, filamentary, or rod-like form dispersed inthe unitary graphene matrix which forms a continuous phase.

The present invention also provides a highly thermally conductiveunitary graphene matrix composite that can be used for thermalmanagement applications; e.g. for use as a heat spreader in amicroelectronic device (such as mobile phone, notebook computer, e-book,and tablet), flexible display, light-emitting diode (LED), power tool,computer CPU, and power electronics. We are filing separate patentapplications to claim the various products or applications of thepresently invented unitary graphene matrix composites.

EXAMPLE 1 Preparation of Nano Graphene Platelets (NGPs) and ExpandedGraphite Flakes

Chopped graphite fibers with an average diameter of 12 μm and naturalgraphite particles were separately used as a starting material, whichwas immersed in a mixture of concentrated sulfuric acid, nitric acid,and potassium permanganate (as the chemical intercalate and oxidizer) toprepare graphite intercalation compounds (GICs). The starting materialwas first dried in a vacuum oven for 24 h at 80° C. Then, a mixture ofconcentrated sulfuric acid, fuming nitric acid, and potassiumpermanganate (at a weight ratio of 4:1:0.05) was slowly added, underappropriate cooling and stirring, to a three-neck flask containing fibersegments. After 16 hours of reaction, the acid-treated graphite fibersor natural graphite particles were filtered and washed thoroughly withdeionized water until the pH level of the solution reached 6. Afterbeing dried at 100° C. overnight, the resulting graphite intercalationcompound (GIC) was subjected to a thermal shock at 1050° C. for 45seconds in a tube furnace to form exfoliated graphite (or graphiteworms).

Five grams of the resulting exfoliated graphite (graphite worms) weremixed with 2,000 ml alcohol solution consisting of alcohol and distilledwater with a ratio of 65:35 for 12 hours to obtain a suspension. Thenthe mixture or suspension was subjected to ultrasonic irradiation with apower of 200 W for various times. After two hours of sonication, EGparticles were effectively fragmented into thin NGPs. The suspension wasthen filtered and dried at 80° C. to remove residue solvents. Theas-prepared NGPs have an average thickness of approximately 9.7 nm.

Another five grams of the resulting exfoliated graphite (EG) weresubjected to low-intensity air jet milling to break up graphite worms,forming expanded graphite flakes (having an average thickness of 139nm).

EXAMPLE 2 Preparation of Single-Layer Graphene from Meso-CarbonMicro-Beads (MCMBs)

Meso-carbon microbeads (MCMBs) were supplied from China Steel ChemicalCo. This material has a density of about 2.24 g/cm³ with a medianparticle size of about 16 μm. MCMB (10 grams) were intercalated with anacid solution (sulfuric acid, nitric acid, and potassium permanganate ata ratio of 4:1:0.05) for 72 hours. Upon completion of the reaction, themixture was poured into deionized water and filtered. The intercalatedMCMBs were repeatedly washed in a 5% solution of HCl to remove most ofthe sulphate ions. The sample was then washed repeatedly with deionizedwater until the pH of the filtrate was neutral. The slurry was dried andstored in a vacuum oven at 60° C. for 24 hours. The dried powder samplewas placed in a quartz tube and inserted into a horizontal tube furnacepre-set at a desired temperature, 1,080° C. for 45 seconds to obtain agraphene material. TEM and atomic force microscopic studies indicatethat most of the NGPs were single-layer graphene.

EXAMPLE 3 Preparation of Pristine Graphene

In a typical procedure, five grams of graphite flakes, ground toapproximately 20 μm or less in sizes, were dispersed in 1,000 mL ofdeionized water (containing 0.1% by weight of a dispersing agent, Zonyl®FSO from DuPont) to obtain a suspension. An ultrasonic energy level of85 W (Branson S450 Ultrasonicator) was used for exfoliation, separation,and size reduction of graphene sheets for a period of 15 minutes to 2hours.

EXAMPLE 4 Preparation of Graphene Oxide (GO) Gel

Graphite oxide gel was prepared by oxidation of graphite flakes with anoxidizer liquid consisting of sulfuric acid, sodium nitrate, andpotassium permanganate at a ratio of 4:1:0.05 at 30° C. When naturalgraphite flakes (particle sizes of 14 μm) were immersed and dispersed inthe oxidizer mixture liquid, the suspension or slurry appears opticallyopaque and dark. The suspension remains opaque during the first 52 hoursof reaction. However, the suspension gradually turns opticallytranslucent (a little cloudy) when the reaction time exceeds 52 hours,and the color of the suspension changes from black to dark brown. After96 hours, the suspension suddenly becomes an optically transparentsolution with light brown color. The solution appears very uniform incolor and transparency, indicating the absence of any dispersed discreteobjects. The whole solution behaves like a gel, very similar to atypical polymer gel.

Surprisingly, by casting this gel on a glass surface and removing theliquid medium from the cast film we obtain a thin film of graphene oxidethat is optically transparent. This thin film looks like, feels like,and behaves like a regular polymer film. However, upon re-graphitizationat a temperature (typically >100° C., more typically >1,000° C., furthertypically >1,500° C., and can be >2,500° C.) for typically 1-3 hours,this GO film is transformed in a unitary graphene entity comprising orbeing a large-size graphene single crystal. This is a free-standingunitary graphene layer, which can be implemented directly as a heatspreader in an electronic device or used as a matrix material in agraphene matrix composite containing a carbon/graphite filler phase.

X-ray diffraction curves of a GO film (GO gel coated on a glass surfacewith liquid medium removed), a GO film thermally reduced at 150° C. forone hour, and a highly reduced and re-graphitized GO film (a unitarygraphene layer) are shown in FIGS. 5(a), 5(b), and 5(c), respectively.The peak at approximately 2θ=12° of the dried GO film (FIG. 5(a))corresponds to an inter-graphene spacing (d₀₀₂) of approximately 0.7 nm.With some heat treatment at 150° C., the GO film exhibits the formationof a hump centered at 22° (FIG. 5(b)), indicating that it has begun theprocess of decreasing the inter-graphene spacing, indicating a partialrecovery of the original structure of natural graphite particles. With aheat treatment temperature of 2,500° C. for one hour, the d₀₀₂ spacinghas decreased to approximately 0.336, close to 0.335 nm of the originalnatural graphite.

The inter-graphene spacing values of GO-derived unitary graphene filmsobtained by heat treating at various temperatures over a widetemperature range are summarized in FIG. 6(a). Corresponding oxygencontent values in the GO-derived unitary graphene layer are shown inFIG. 6(b). The thermal conductivity of GO-derived unitary graphene layerand corresponding flexible graphite (FG) foil, also plotted as afunction of the same final heat treatment temperature range issummarized in FIG. 6(c). It is of significance to point out that a heattreatment temperature as low as 500° C. is sufficient to bring theaverage inter-graphene spacing in GO back to below 0.4 nm, gettingcloser and closer to that of natural graphite. The beauty of thisapproach is the notion that this GO gel strategy has enabled us tore-organize, re-orient, and chemically merge the graphene planes ofcarbon atoms from originally different graphite flakes or graphenesheets into a graphene monolith with all the graphene planes now beinglarger in lateral dimensions (larger than the length and width oforiginal graphene planes) and essentially parallel to one another. Thishas given rise to a thermal conductivity already >420 W/mK (>950 W/mkwith a heat treatment temperature of 700° C.), which is more than 2- to4-fold the value (200 W/mK) of the corresponding flexible graphite foil.These graphene planes of carbon atoms are derived and merged from thegraphene planes that constitute the original natural graphite structure.The original natural graphite particles, when randomly packed into anaggregate or “graphite compact”, have their constituent graphene planesrandomly oriented, exhibit relatively low thermal conductivity, and haveessentially zero strength (no structural integrity). In contrast, thestrength of the unitary graphene layer is typically in the range of40-140 MPa.

With a heat treatment temperature as low as 800° C., the resultingunitary graphene layer exhibits a thermal conductivity of 1,148 W/mK, incontrast to the 244 W/mK of the flexible graphite foil with an identicalheat treatment temperature. As a matter of fact, no matter how high theheat treatment temperature is (e.g. even as high as 2,800° C.), theflexible graphite foil only shows a thermal conductivity lower than 600W/mK. At a heat treatment temperature of 2,800° C., the presentlyinvented unitary graphene layer delivers a thermal conductivity of 1,807W/mK (FIG. 4(a) and FIG. 6(c)).

A close scrutiny and comparison of FIGS. 2(a), 3(a), and 3(b) indicatesthat the graphene layers in a graphene single crystal or graphenemonolithic are substantially oriented parallel to one another; but thisis not the case for flexible graphite foils and graphene oxide paper.The inclination angles between two identifiable layers in the unitarygraphene entity are mostly less than 5 degrees. In contrast, there areso many folded graphite flakes, kinks, and mis-orientations in flexiblegraphite that many of the angles between two graphite flakes are greaterthan 10 degrees, some as high as 45 degrees (FIG. 2(b)). Although notnearly as bad, the mis-orientations between graphene platelets in NGPpaper (FIG. 3(b)) are also high and there are many gaps betweenplatelets. The unitary graphene entity is essentially gap-free.

FIG. 4(a) shows the thermal conductivity values of the GO-derivedunitary graphene matrix layer (▴), GO paper (▪) prepared byvacuum-assisted filtration of RGO, and FG foil (♦), respectively, allplotted as a function of the final heat treatment temperature forgraphitization or re-graphitization. These data have clearlydemonstrated the superiority of the unitary graphene layer or graphenesingle crystal in terms of the achievable thermal conductivity at agiven heat treatment temperature. All the prior art work on thepreparation of paper or membrane from pristine graphene or grapheneoxide sheets/platelets follows distinctly different processing paths,leading to a simple aggregate or stack of discrete graphene or GO/RGOplatelets. These simple aggregates or stacks exhibit many foldedgraphite flakes, kinks, gaps, and mis-orientations, resulting in poorthermal conductivity, low electrical conductivity, and weak mechanicalstrength. As shown in FIG. 4(a), even at a heat treatment temperature ashigh as 2,800° C., the GO paper exhibits a thermal conductivity lessthan 1,000 W/mK, much lower than the >1,800 W/mK of the GO gel-derivedunitary graphene entity.

For comparison, we also carbonized polyimide films at 500° C. for 1 hourand at 1,000° C. for 3 hours in an inert atmosphere and then graphitizedthe films at a temperature in the range of 2,500-3,000° C. for 1 to 5hours to form a conventional graphitic film, pyrolytic graphite (PG).FIG. 4(b) shows the thermal conductivity values of the GO-derivedunitary graphene layer (▪) and the polyimide-derived pyrolytic graphite(PG) heat-treated for one hour (x) and for 3 hours (▴), all plotted as afunction of the final graphitization or re-graphitization temperature.These data show that the conventional pyrolytic graphite (PG), producedby carbonizing polyimide and then graphitizing the carbonized PI,exhibits a consistently lower thermal conductivity as compared to theGO-derived unitary graphene layer alone (▪), given the same heattreatment (graphitization or re-graphitization) temperature for the samelength of heat treatment time. For instance, the PG from PI exhibits athermal conductivity of 820 W/mK after a graphitization treatment at2,000° C. for one hour and 1,242 W/mK at 2,000° C. for 3 hours. Theseobservations have demonstrated a clear and significant advantage ofusing the GO gel approach versus the conventional PG approach. As amatter of fact, no matter how long the graphitization time is for thePG, the thermal conductivity is always lower than that of a GOgel-derived unitary graphene layer. In other words, the unitary graphenelayer is fundamentally different and patently distinct from the flexiblegraphite (FG) foil, graphene/GO/RGO paper/membrane, and pyrolyticgraphite (PG) in terms of chemical composition, structure, morphology,process of production, and properties.

The above conclusion is further supported by the data in FIG. 4(c)showing the electric conductivity values of the GO-derived unitarygraphene layer (♦) are far superior to those of the GO paper (▪) fromRGO platelets and FG foil (x) over the entire range of finalgraphitization or re-graphitization temperatures investigated.

EXAMPLES 5 Preparation and Testing of Graphene Matrix Composites

GO gel can be combined with a carbon/graphite filler phase to form agraphene matrix composite. The graphene oxide gel prepared in Example 4was used for the preparation of graphene matrix composite. Theexfoliated graphite flakes prepared in Examples 1 were made into thinporous paper or film form (e.g., using a vacuum-assisted filtrationtechnique) for use as a carbon/graphite filler. Other carbon or graphitefillers investigated include carbon nano-tubes and CNT paper (Buckypaper from Buckeye Composites, Inc., Dayton, Ohio), carbon nano-fibersand CNF mats (CNFs supplied from Applied Sciences, Inc., Cedarville,Ohio), flexible graphite foils of several different thicknesses(supplied from Graftech and Timcal Graphite), carbon fibers and carbonfiber mats, woven fabrics of graphite fibers, carbon paper (Toray), MCMBparticles, carbon black (CB), acetylene black (AB), and needle coke.

Two approaches were adapted to produce graphene matrix composites. Inthe first approach, the particles of the carbon/graphite filler phasewere formed into porous pre-forms, such as porous paper, mat, and fabric(woven or non-woven). The porous pre-form was then impregnated with GOgel, which was followed by drying and heat treating.

In a second approach, discrete particles or fibers of thecarbon/graphite filler phase were added into the GO gel to form amixture gel or gel slurry. Pure GO gel or carbon/graphite filler-GOmixture gel or slurry was then cast onto a solid substrate surface usinga coating machine equipped with drying and heating provisions. In somecases, the GO gel or filler-GO gel mixture was casted onto a substrateand regulated by a doctor's blade to form a uniform coating thereon. Theliquid in the coating was further removed in a vacuum oven to form asolid GO coating. The resulting GO or GO-filler layers were thensubjected to a heat treatment at a temperature of from 100° C. up toapproximately 3,000° C. We have utilized several temperature regimes:100° C.-1,000° C.; 1,000° C.-1,500° C.; 1,500° C.-2,500° C.; and 2,500°C.-3,000° C.

EXAMPLES 6 Electrical and Thermal Conductivity Measurements of VariousGraphene Oxide-Derived Unitary Graphene and Graphene Matrix CompositeLayers

Four-point probe tests were conducted on unitary graphene matrixcomposites (e.g. containing CNT, expanded graphite flakes, carbon black,etc), the GO-derived unitary graphene layer alone (coated on a glasssurface and then peeled off and heat treated), GO/RGO paper, and the FGfoils alone to measure their in-plane electrical conductivity. Theirin-plane thermal conductivity was measured using a laser flash method(Netzsch Thermal Diffusivity Device).

The in-plane thermal and electrical conductivities and tensileproperties of various films or laminates were investigated. Severalsignificant observations can be made from the testing results (e.g. assummarized in FIGS. 4(d), 4(e), 8(a), 8(b), 9(a), and 9(b)):

-   -   (1) With a thickness of approximately 75 μm, the thermal        conductivity of the flexible graphite foil alone (FG, ▴ in FIG.        4(a)) is less than 237 W/mK if the FG foil is not heat-treated        at or above 700° C. As the post-recompression heat treatment        temperature increases from 700° C. to 2,800° C. (for one hour of        graphitization treatment in each case), the thermal conductivity        of the FG foil increases from 237 to 582 W/mK, indicating some        but limited re-organization of the graphitic structure induced        by the heat treatment. By contrast, the thermal conductivity of        the GO-derived unitary graphene layer alone increases from 983        to 1,807 W/mK (▪ in FIG. 8(a)). This unitary graphene matrix        material is obtained by shearing and depositing a layer of GO        gel on a glass surface, removing the liquid from the GO layer in        vacuum for 1 hour, and peeling off the dried solid GO layer from        the glass surface. This indicates a significant or dramatic        re-organization of the graphitic structure induced by the heat        treatment, with all GO molecules linked or merged edge-to-edge        and face-to-face into unitary graphene layers and integrated        into a unitary entity of fully and orderly bonded graphene        planes, a graphene single crystal.    -   (2) The experimentally measured thermal conductivity of a        corresponding series of GO-derived unitary graphene matrix        composite containing expanded graphite flakes as the filler        phase (♦ in FIG. 8(a)) increases from approximately 800 to 1,800        W/mK. This is significantly higher than the thermal conductivity        values of what would be theoretically predicted (x in FIG. 8a ))        from a rule-of-mixture law, which is commonly used to predict        composite properties from constituent properties. These data        have clearly demonstrated an un-expected, synergistic effect        between GO-derived unitary graphene matrix (derived from        graphene oxide gel) and the dispersed expanded graphite flakes.

Also shown in FIG. 8(a) are the thermal conductivity data ofcorresponding flexible graphite foil (FG prepared by roll-pressing ofexfoliated graphite worms) and foil of expanded graphite flakes(prepared by breaking up graphite worms into graphite flakes asdescribed in Example 1, which were then packed and roll-pressed into athin foil). The highest thermal conductivity value achievable with theexpanded graphite foil is <800 W/mK and that with FG is <600 W/mK, bothbeing dramatically lower than those of both the unitary graphene matrixand the graphene matrix composite.

-   -   (3) FIG. 8(b) shows that the conventional pyrolytic graphite        (PG), produced by carbonizing polyimide, roll-pressing, and then        graphitizing the carbonized PI, exhibits a consistently lower        thermal conductivity as compared to the GO-derived unitary        graphene layer alone (▪) or unitary graphene matrix composite        (♦), given the same heat treatment (graphitization or        re-graphitization) temperature for the same length of heat        treatment time. For instance, the PG from PI exhibits a thermal        conductivity of 820 W/mK after a graphitization treatment at        2,000° C. for one hour and 1,242 W/mK at 2,000° C. for 3 hours.        These observations have demonstrated a clear and significant        advantage of using the GO gel approach versus the conventional        PG approach. As a matter of fact, no matter how long the        graphitization time is for the PG, the thermal conductivity is        always lower than that of a GO gel-derived unitary graphene or        unitary graphene matrix composite. Clearly, both the GO-derived        unitary graphene layer and unitary graphene matrix composite are        fundamentally different and patently distinct from the pyrolytic        graphite in terms of chemical composition, structure,        morphology, process of production, and properties.    -   (4) FIG. 4(d) shows the thermal conductivity values of both        unitary graphene matrix and graphene matrix-CNT composite are        far superior to those of prior art GO paper containing discrete        GO platelets and those of GO paper containing an equal        proportion of the same CNTs (approximately 26% by weight). FIG.        4(e) demonstrates that unitary graphene matrix composite        containing carbon black particles as the carbon/graphite filler        phase are significantly higher than those of prior art GO paper        and corresponding GO-CB paper.

EXAMPLES 7 Tensile Strength of Various Graphene Oxide-Derived UnitaryGraphene Matrix Composites

A series of GO-derived unitary graphene layers, graphene matrixcomposites, GO paper, and FG foil were prepared. A universal testingmachine was used to determine the tensile strength of these materials.The tensile strength values of the unitary graphene entity, GO paper,and FG paper are plotted as a function of the re-graphitizationtemperature, FIG. 9(a). These data have demonstrated that the tensilestrength of the flexible graphite foil remains relatively constant (all<20 MPa) and that of the GO paper increases slightly (from 22 to 43 MPa)when the heat treatment temperature increases from 700 to 2,800° C. Incontrast, the tensile strength of the GO-derived unitary graphene layerincreases dramatically from 32 to >100 MPa over the same range of heattreatment temperatures. This result is quite striking and furtherreflects the notion that the GO gel-derived GO layer contains highlyalive and active molecules during the heat treatment, while the grapheneplatelets in the GO paper and the graphite flakes in the FG foil areessentially dead molecules. The GO-derived unitary graphene entity orgraphene single crystal is a class of material by itself.

The tensile strength values of three unitary graphene matrix compositeswith the final re-graphitization temperature of 1,500° C. are plotted asa function of the filler weight fraction for three carbon/graphitefiller types: CNT, expanded graphite flakes, and carbon black particles(FIG. 9(b)). Although adding CNTs to the unitary graphene matrixdecreases the thermal conductivity (FIG. 4(d)), the strength of theresulting composites increases monotonically with (actually proportionalto) the CNT weight fraction, reaching a value of 200 MPa that is oneorder of magnitude higher than the typical strength of flexiblegraphite-type materials. This is completely unexpected.

This appears to suggest that GO molecules have a strong adhering powercapable of bonding to CNTs, creating a strong interfacial bond to assistin the load transfer and enabling CNTs to carry a significant proportionof the mechanical force imposed upon the composite. It may be noted thatepoxy matrix composites containing multi-walled carbon nanotubes as thereinforcement phase have never exhibit a tensile strength higher than 80MPa. This is partially due to the difficulty of dispersing CNTs in apolymer, to the extent that it has been extremely difficult towell-disperse more than 5% by weight of CNTs in epoxy. Beyond 5% byweight, CNTs could not be homogeneously dispersed in epoxy and thetensile strength actually begins to decrease with increasing CNT weightpercentage. The observation that CNTs can be well dispersed in thegraphene matrix up to 30% by weight is shocking, indicating outstandingchemical compatibility between GO molecules and discrete CNT filaments.Further shocking is the 200 MPa tensile strength exhibited by thegraphene matrix-CNT composite, a value that no reinforced epoxycomposite has been able to achieve unless the reinforcement phase (suchas high-strength carbon fibers) is well aligned in the loading direction(e.g. in a unidirectional fiber composite).

EXAMPLES 8 The Surface Scratch Resistance (in Terms of ScratchVisibility and Scratch Depth), and Hardness of Various Unitary GrapheneMatrix Composites

The scratch test was conducted using the so-called Ford Lab Test Method(FLTM) BN108-13. This apparatus consists of a movable platform connectedto five beams with 250 mm in length. A scratch pin is attached to oneend of each beam. A highly polished hardened steel ball (1.0±0.1 mmdiameter) is placed on the tip of each pin. Each pin is loaded with aweight that exerts a force of 7N, 6N, 3N, 2N, and 0.6N, respectively.Driven by compressed air, the beams draw the pins across the specimensurface and generate scratches. The scratch is made at a slidingvelocity of approximately 100 mm/s. All tests were performed at roomtemperature. Although the test method requires that grained surfaces beevaluated, only the smooth surfaces of the specimens were tested in thisstudy.

After the specimen plaques were scratched, they were evaluated with areflected light polarizing microscope incorporating a Xenon lightsource. An image analyzer with Image Analysis Software was used tomeasure the “gray scale mass,” which is the total gray scale value ofthe object. The camera objective lens is positioned at an angle of 90°from the scratch. The objective lens then registers a portion of thescratch about 1 mm long. The electron signal for each scratch line isthen integrated and recorded. The optical mass of an object, M, is thesum of the gray level values, GL, of all pixels in the object. Theindividual gray level values are assigned by the image analysis programin unit steps in the range of 0-255, where 0=black and 255=white. Theoptical mass, M, can be computed from: M=ΣGL_(i) (sum over i to n),where n is the number of pixels. The brightness of the object, B, isB=M/A, where A represents the area of the object. The percentage changein the brightness between the scratch and the background is the scratchvisibility, ΔB, given byΔB=[(B_(scratch)−B_(background))/(B_(background))]×100%. The depth ofthe scratch was measured using an interferometer. The magnification wasset at 5×. Depth measurements were made from the depth histogram of thescanned area. The scratches were also examined using a scanning electronmicroscope (SEM).

Indentation hardness tests were also performed on selected specimens.For the Rockwell Hardness test, the ASTM D 785 test procedure wasfollowed. The indenter was a round steel ball with 12.5 mm in diameter(Rockwell R scale). The Rockwell hardness number is a measure of thenon-recoverable indentation after a heavy load of 588N for a period of15 s, and subsequently reduced to a minor load of 98N for anotherduration of 15 s. Normal hardness is then defined as the load divided bythe projected area.

FIGS. 9(c) and 9(d) show the Rockwell hardness and scratch depth data,respectively, of several graphene matrix composites plotted as afunction of the filler weight percentage (FIG. 9(c)) andre-graphitization temperature (FIG. 9(d)). The Rockwell hardness data inFIG. 9(c) are found to be well correlated with the tensile strength dataof FIG. 9(b). Again, the presence of CNTs can significantly increase thehardness of the unitary graphene matrix. The scratch resistance of theunitary graphene matrix can also be significantly improved by addingsome CNT (20% by weight as in FIG. 9(d)). This improvement is diminishedas the final re-graphitization temperature exceeds 1,000 C wherein theunitary graphene matrix alone is already of high strength and hardness.

EXAMPLES 9 Heat Dissipation Systems Containing a Graphene Oxide-DerivedUnitary Graphene

We have used an infrared thermography-based hand-help device to measurethe surface temperatures of a range of microelectronic devices, such assmart phones and laptop computer. For instance, FIG. 7 shows the surfacetemperature fields of two identical smart phones running the same videoprograms for 10 minutes. One smart phone (top image) contains 2 sheetsof flexible graphite (FG) foils between the CPU and the casing, showingan external surface temperature as high as 38.6° C. The internaltemperature near the CPU is presumably much higher than 60 or 70° C., adangerous temperature that could eventually damage the device. Incontrast, the other smart phone (bottom image) contains one sheet ofGO-derived unitary graphene-coated FG foil, showing an external surfacetemperature of 25.4° C. This example has vividly demonstrated theeffectiveness of implementing a unitary graphene-based material as aheat-spreader layer in a thermal management system. A similarimprovement was observed when a layer of graphene matrix compositecontaining graphite flake filler was used.

EXAMPLES 10 Thermal and Electrical Properties of Various UnitaryGraphene Matrix Composites

The thermal and electric conductivities of graphene matrix compositescontaining various carbon or graphite fillers in different forms aresummarized in Table 1 below. Given the same final heat treatmenttemperature, all the graphene matrix composites exhibit better electricand thermal conductivities as compared to the baseline flexible graphitefoil and GO paper.

TABLE 1 In-plane thermal and electric conductivities Re-graphi- ThermalElectric tization conduc- conduc- temperature Filler type, form, tivitytivity Sample No. (° C.) and wt. % (W/mK) (S/cm) 31-G 1,500 None 1,6104,200 31-G-AB 1,500 Acetylene black 946 3,550 particles, dispersed, 35%31-G-MCMB 1,500 Particles, 1,156 3,605 dispersed, 25% 31-G-Coke 1,500Needle coke, 1,028 3,002 dispersed, 25% 32-G 2,500 None 1,736 10,30032-G-CNF 2,500 CNF, mat, 10% 1,550 9,213 32-G-CF-Uni 2,500 Continuouscarbon 1,250 7,250 fibers, unidirec- tional, 55% 32-G-CF-W 2,500Continuous carbon 1,143 6,037 fibers, woven fabric, 54% 32-G-CF-Ch 2,500Chopped carbon 1,057 5,454 fiber, mat, 45% 32-G-AC 2,500 Activatedcarbon, 1,611 9,763 dispersed, 15% FG foil 2,500 — 560 2,300 GO paper2,500 — 920 3,500

As indicated in FIGS. 8(a) and 8(b), the presently invented unitarygraphene matrix composites do not have to go through anultra-high-temperature graphitization treatment to achieve a highthermal conductivity (e.g. K already=988 W/mK with T=800° C. and K=1,487W/mK with T=1,250° C.). Graphitization of a carbonized resin (e.g.polyimide) or other carbon materials requires a temperature typicallyhigher than 2,000° C., most typically higher than 2,500° C. Thegraphitization temperature is most typically in the range of2,800-3,200° C. in order for carbonized materials or pyrolytic graphiteto achieve a thermal conductivity of 1,600-1,700 W/mK. In contrast, thetypical heat treatment temperature (re-graphitization treatment) of thepresently invented GO-coated laminates is significantly lower than2,500° C. and more typically lower than 1,500° (can be as low as100-150° C.).

For instance, polyimide (PI), if carbonized and graphitized for 5 hours(including 4 hours for carbonization at 1,000-1,500° C. andl hour forgraphitization at 2,000° C.), exhibits a thermal conductivity of 820W/mK. In contrast, we were able to reach a thermal conductivity of 988W/mK with a heat treatment of graphene matrix composite at 800° C. for atotal of two hours. This is very surprising and no one has ever thoughtthat such a low graphitization temperature was possible. Further, a heattreatment of the GO-derived unitary graphene-matrix composite at thesame 2,000° C. for 1 hour imparts a thermal conductivity of 1,680 W/mK(vs. 820 W/mK of the carbonized PI). Clearly, this is a dramaticallyfaster, less energy-intensive, and more cost-effective process. Theresulting products are also far superior to pyrolytic graphite. Theunitary graphene matrix composites, the unitary graphene layer itself(from GO gel), and the pyrolytic graphite are three fundamentallydifferent and patently distinct classes of materials in terms ofchemical composition, morphology, structure, process of production, andvarious properties.

In conclusion, we have successfully developed an absolutely new, novel,unexpected, and patently distinct class of highly conducting material:graphene oxide gel-derived unitary graphene matrix composite. Thechemical composition, structure, morphology, process of production, andproperties of this new class of materials are fundamentally differentand patently distinct from flexible graphite foil, polymer-derivedpyrolytic graphite, CVD-derived PG (including HOPG), and catalytic CVDgraphene thin film. The thermal conductivity, electrical conductivity,scratch resistance, surface hardness, and tensile strength exhibited bythe presently invented materials are much higher than what prior artflexible graphite sheets, graphene or GO paper, or other graphitic filmscould possibly achieve. These GO-derived unitary graphene materials havethe best combination of excellent electrical conductivity, thermalconductivity, mechanical strength, surface scratch resistance, hardness,and no tendency to flake off.

We claim:
 1. A graphene matrix composite comprising: a. a single crystalgraphene matrix material, containing closely packed and chemicallybonded graphene planes having an inter-graphene plane spacing of 0.335to 0.40 nm and an oxygen content of 0.001% to 10% by weight; b. a carbonor graphite filler phase selected from a carbon or graphite fiber,carbon or graphite nanofiber, carbon nanotube, carbon nanorod, mesophasecarbon particle, mesocarbon microbead, exfoliated graphite flake with athickness greater than 100 nm, exfoliated graphite or graphite worm,coke particle, needle coke, carbon black or acetylene black particle,activated carbon particle, or a combination thereof; wherein the fillerphase is covalently bonded to the matrix material, and wherein thefiller phase has a weight fraction of 0.01% to 99% based on the totalcomposite weight.
 2. A graphene matrix composite comprising: (a) apolycrystalline graphene matrix material having incomplete grainboundaries, containing closely packed and chemically bonded grapheneplanes having an inter-graphene plane spacing of 0.335 to 0.40 nm and anoxygen content of 0.001% to 10% by weight; (b) a carbon or graphitefiller phase selected from a carbon or graphite fiber, carbon orgraphite nanofiber, carbon nanotube, carbon nanorod, mesophase carbonparticle, mesocarbon microbead, exfoliated graphite flake with athickness greater than 100 nm, exfoliated graphite or graphite worm,coke particle, needle coke, carbon black or acetylene black particle,activated carbon particle, or a combination thereof; wherein the fillerphase is covalently bonded to the matrix material, and wherein thefiller phase has a weight fraction of 0.01% to 99% based on the totalcomposite weight.
 3. The graphene matrix composite of claim 2 having athickness from 10 nm to 200 μm.
 4. The graphene matrix composite ofclaim 2 having a density from 1.5 g/cm³ to 2.0 g/cm³, a porosity from 5%to 20%, or both.
 5. The graphene matrix composite of claim 2 having athermal conductivity from 600 W/mK to 1,750 W/mK
 6. The graphene matrixcomposite of claim 2 having an electrical conductivity from 2,000 S/cmto 10,000 S/cm.
 7. The graphene matrix composite of claim 2 having atensile strength from 40 to 200 MPa.
 8. The graphene matrix composite ofclaim 2 having a Rockwell surface hardness from 60 to
 100. 9. Thegraphene matrix composite of claim 2 wherein the graphene planes of thematrix material have a crystallographic c-axis having an averagemiss-orientation angle of less than 10 degrees or wherein the grapheneplanes of the matrix material are essentially parallel to each other.10. The graphene matrix composite of claim 2 having graphene crystalsfrom 100 microns to 1 cm in size.
 11. The graphene matrix composite ofclaim 2 wherein the matrix material is a two dimensional or threedimensional network.
 12. The graphene matrix composite of claim 2wherein the filler phase has a particulate, filamentary, or rod-likeform.
 13. The graphene matrix composite of claim 2 wherein the fillerphase is aligned along a direction to create anisotropy.
 14. Thegraphene matrix composite of claim 2 wherein the filler phase is aporous mat, a porous web, a porous preform, a porous paper, a nonwovenfabric, or a woven fabric.
 15. A process for producing a graphene matrixcomposite comprising a polycrystalline graphene matrix material havingincomplete grain boundaries, and having closely packed and chemicallybonded graphene planes with an inter-graphene plane spacing of 0.335 to0.40 nm, and an oxygen content of 0.001% to 10% by weight; said processcomprising: a. preparing a graphene oxide gel having graphene oxidemolecules dispersed in a fluid medium; b. mixing a carbon or graphitefiller phase into said graphene oxide gel to form a slurry; c.dispensing said slurry onto a surface of a supporting substrate or acavity of a molding tool to form a wet composite precursor; d. partiallyor completely removing the fluid medium from the wet composite precursorto form a composite precursor; and e. heat treating the compositeprecursor at a temperature from 100° C. to 3,000° C. to form thegraphene matrix composite.
 16. The process of claim 15 where the wetcomposite precursor has a thickness of 500 μm to 10 mm prior to drying.17. The process of claim 15 further comprising a step of applied vacuumto remove some of the fluid medium from the wet composite precursor. 18.The process of claim 15 further comprising a step of compression duringor after the step of heat treatment.
 19. The process of claim 15 where ashear stress is applied during dispensing or forming of a wet compositeprecursor.
 20. A process for producing a graphene composite monolith orsheet comprising a polycrystalline graphene matrix material havingincomplete grain boundaries, and having closely packed and chemicallybonded graphene planes with an inter-graphene plane spacing of 0.335 to0.40 nm, and an oxygen content of 0.001% to 10% by weight; said processcomprising: a. preparing a graphene oxide gel having graphene oxidemolecules dispersed in a fluid medium; b. impregnating the grapheneoxide gel into a porous mat, web, perform, paper or fabric to form a wetcomposite precursor; c. dispensing the wet composite precursor onto asurface of a supporting substrate or a cavity of a molding tool to forma shaped wet composite precursor; d. partially or completely removingthe fluid medium from the shaped wet composite precursor to form acomposite precursor; and e. heat treating the composite precursor at atemperature from 100° C. to 3000° C. to form the graphene compositemonolith or sheet, wherein the mat, web, perform, paper or fabricoccupies a weight fraction from 1% to 99% after heat treatment.